WO2018216771A1 - Brazing method for aluminum alloy brazing sheet and method for producing heat exchanger - Google Patents

Brazing method for aluminum alloy brazing sheet and method for producing heat exchanger Download PDF

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Publication number
WO2018216771A1
WO2018216771A1 PCT/JP2018/020021 JP2018020021W WO2018216771A1 WO 2018216771 A1 WO2018216771 A1 WO 2018216771A1 JP 2018020021 W JP2018020021 W JP 2018020021W WO 2018216771 A1 WO2018216771 A1 WO 2018216771A1
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Prior art keywords
brazing
mass
less
content
aluminum alloy
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PCT/JP2018/020021
Other languages
French (fr)
Japanese (ja)
Inventor
孝裕 泉
鶴野　招弘
申平 木村
雄二 渋谷
貴弘 篠田
詔悟 山田
慎吾 大野
Original Assignee
株式会社神戸製鋼所
株式会社デンソー
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Application filed by 株式会社神戸製鋼所, 株式会社デンソー filed Critical 株式会社神戸製鋼所
Priority to CN201880034076.2A priority Critical patent/CN110662626A/en
Priority to EP18806867.0A priority patent/EP3636380B1/en
Priority to US16/616,308 priority patent/US20200086430A1/en
Publication of WO2018216771A1 publication Critical patent/WO2018216771A1/en

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
    • B23K35/0222—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in soldering, brazing
    • B23K35/0233—Sheets, foils
    • B23K35/0238—Sheets, foils layered
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K1/00—Soldering, e.g. brazing, or unsoldering
    • B23K1/0008—Soldering, e.g. brazing, or unsoldering specially adapted for particular articles or work
    • B23K1/0012—Brazing heat exchangers
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K1/00—Soldering, e.g. brazing, or unsoldering
    • B23K1/008—Soldering within a furnace
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K1/00—Soldering, e.g. brazing, or unsoldering
    • B23K1/19—Soldering, e.g. brazing, or unsoldering taking account of the properties of the materials to be soldered
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
    • B23K35/286—Al as the principal constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/04—Tubular or hollow articles
    • B23K2101/14—Heat exchangers
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/08—Non-ferrous metals or alloys
    • B23K2103/10—Aluminium or alloys thereof
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
    • F28F21/081—Heat exchange elements made from metals or metal alloys
    • F28F21/084—Heat exchange elements made from metals or metal alloys from aluminium or aluminium alloys
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F2275/00—Fastening; Joining
    • F28F2275/04—Fastening; Joining by brazing

Definitions

  • the present invention relates to a method of brazing an aluminum alloy brazing sheet and a method of manufacturing a heat exchanger, and in particular, a flux-free brazing method, a so-called fluxless brazing method, and a fluxless brazing method
  • the present invention relates to a method of manufacturing a heat exchanger.
  • brazing members such as aluminum alloy heat exchangers
  • vacuum brazing in which brazing is performed without using flux in a vacuum.
  • This vacuum brazing has various merits such as the necessity of the process of applying the flux and the avoidance of the problem caused by the inappropriate application amount of the flux as compared with the flux brazing using the flux.
  • vacuum brazing requires an expensive vacuum furnace to heat the furnace in a vacuumed state at the time of brazing, which increases the operation cost and makes it difficult to control the vacuumed furnace. This makes the work more difficult.
  • an aluminum clad material in which an Al—Si-based brazing material containing 0.1 to 5.0% of Mg and 3 to 13% of Si by mass% is located on the outermost surface.
  • a method of brazing a heat exchanger having narrow channel inner fins wherein the Si particles contained in the Al-Si-based brazing material have a circle equivalent diameter of those having a diameter of 0.8 ⁇ m or more.
  • the Al-Si-based brazing material is brought into close contact with the brazing target member in a non-oxidizing atmosphere with a pressure of 25% or more and a diameter of 75 ⁇ m or more at a heating temperature of 559 to 620 ° C.
  • a fluxless brazing method of a heat exchanger having narrow channel inner fins characterized in that the aluminum clad material and the brazing target member are joined.
  • the technique according to Patent Document 1 relates to fluxless brazing in an inert gas atmosphere that is not a vacuum, and is examining a predetermined effect.
  • the technology according to Patent Document 1 can not exhibit sufficient brazeability.
  • the brazing material contains 0.1 to 3% by mass of Mg, and this Mg is in the temperature rising process at the time of the brazing addition heat. And promote the formation of MgO on the surface of the brazing material.
  • MgO on the surface of the brazing material may become an obstacle at the time of brazing and melting, and the brazing property may be reduced.
  • this invention makes it a subject to provide the brazing method of the aluminum alloy brazing sheet which can exhibit the outstanding brazing property, and the manufacturing method of a heat exchanger.
  • the core material of the aluminum alloy brazing sheet used and the content of the components of the brazing material for example, the Mg content of the core and brazing material and the brazing material Since the relationship with the content of Bi, etc. is specified, the formation of MgO on the surface of the brazing material is suppressed by the reaction (trap) of Mg of the core material and the brazing material with Bi of the brazing material. .
  • Mg which has reacted with Bi dissolves in the matrix (brazing material) during brazing and melting when brazing is applied heat, so evaporation of Mg is promoted, and the oxide film formed on the brazing material surface is evaporated during Mg evaporation.
  • the brazing material is Mn: 2.0 mass% or less, Ti: 0.3 mass% or less, Cr: 0.3 mass% or less, Zr: You may further contain 1 or more types in 0.3 mass% or less. In the brazing method of the aluminum alloy brazing sheet according to the present invention, the brazing material may further contain Zn: 5.0% by mass or less.
  • the brazing material may further contain rare earth element: 1.0% by mass or less.
  • the brazing method of the aluminum alloy brazing sheet according to the present invention is excellent in brazeability even if the brazing material contains Mn, Ti, Cr, Zr, Zn, Sr, Na, Sb, and a rare earth element. Can be demonstrated.
  • the brazing material may further contain 0.3 mass% or less of Li.
  • the brazing method of the aluminum alloy brazing sheet according to the present invention can further improve the brazing property because the brazing material contains Li.
  • the core material may further contain Mn: 2.5% by mass or less.
  • the core material may further contain Si: 1.2% by mass or less.
  • the core material may further contain Cu: 3.0 mass% or less.
  • the core material may further contain Fe: 1.5% by mass or less.
  • the core material is at least one of Ti: 0.5% by mass or less, Cr: 0.5% by mass or less, and Zr: 0.5% by mass or less May further be contained.
  • the brazing method for an aluminum alloy brazing sheet according to the present invention can exhibit excellent brazing properties even if the core material contains Mn, Si, Cu, Fe, Ti, Cr, or Zr. .
  • the core material may further contain 0.3 mass% or less of Li.
  • the brazing method of the aluminum alloy brazing sheet according to the present invention can further improve the brazing property because the core material contains Li.
  • the thickness of the brazing material may be 50 ⁇ m or more.
  • the brazing method of the aluminum alloy brazing sheet according to the present invention can more reliably exhibit excellent brazing property because the thickness of the brazing material is a predetermined value or more.
  • a method of manufacturing a heat exchanger according to the present invention includes a brazing step of performing the above-described brazing method.
  • the manufacturing method of the heat exchanger which concerns on this invention can manufacture a heat exchanger, exhibiting excellent brazability by including the brazing process which implements a predetermined
  • the brazing method of the aluminum alloy brazing sheet according to the present invention can exhibit excellent brazing properties by specifying the contents of the respective components of the core material and the brazing material of the aluminum alloy brazing sheet to be used.
  • the manufacturing method of the heat exchanger according to the present invention manufactures a heat exchanger while exhibiting excellent brazing property because the content of each component of the core material and brazing material of the aluminum alloy brazing sheet to be used is specified. can do.
  • an aluminum alloy brazing sheet (hereinafter, appropriately referred to as a “brazing sheet”) used for a method of brazing an aluminum alloy brazing sheet according to the present embodiment (hereinafter, appropriately referred to as “brazing method”) will be described.
  • the configuration of the brazing sheet according to the present embodiment includes, for example, as shown in FIG. 1, a core material 2 and a brazing material 3 provided on one surface of the core material 2. And as for the brazing sheet 1 which concerns on this embodiment, content of each component of the core material 2 and the brazing material 3 is specified suitably.
  • the reasons for numerical limitation of each component of the core and brazing material of the brazing sheet according to the present embodiment will be described in detail.
  • the core material of the brazing sheet according to the present embodiment is made of an aluminum alloy (including pure aluminum), and more specifically, an aluminum alloy having Mg of 2.0% by mass or less (including 0% by mass).
  • an aluminum alloy an Al-Cu alloy of JIS 2000 series, an Al-Mn alloy of JIS 3000 series, an Al-Mg alloy of JIS 5000 series, an Al-Mg-Si alloy of JIS 6000 series, etc. Can be used.
  • the core material of the brazing sheet according to the present embodiment may further contain Mn, Si, Cu, Fe, Ti, Cr, Zr, and Li as appropriate.
  • Mg in core 2.0 mass% or less
  • Heartwood Mg improves strength.
  • Mg of the core material diffuses to the brazing material during the heating process at the time of heat addition to the brazing material, evaporates into the atmosphere at the brazing melting temperature, and reacts with oxygen in the atmosphere.
  • the oxide film formed on the surface of the brazing material is suitably destroyed at the time of evaporation of Mg, and the oxygen concentration in the atmosphere is lowered to suppress reoxidation of molten brazing (getter action).
  • Mg of the brazing material also exerts a getter action, when the content of Mg of the brazing material is large, the content of Mg of the core material may be small, or may be 0 mass%.
  • the content of Mg in the core material is 2.0% by mass or less (including 0% by mass).
  • Mn of core material 2.5 mass% or less
  • the core material Mn improves the strength. However, when the content of Mn exceeds 2.5% by mass, the amount of the Al—Mn-based compound increases, and there is a possibility that a crack may occur during the material manufacturing process. Therefore, when the core material contains Mn, the content of Mn is 2.5% by mass or less.
  • Si of core less than 1.2% by mass
  • the core material Si improves the strength. However, if the content of Si exceeds 1.2% by mass, the solidus temperature of the core material is lowered, so that the erosion resistance is lowered and the solderability is lowered, so that the brazing property is lowered. Accordingly, when the core material contains Si, the content of Si is 1.2% by mass or less.
  • the core material Cu makes the potential of the core material noble and improves the corrosion resistance. However, if the content of Cu exceeds 3.0% by mass, the solidus temperature of the core material is lowered, so that the erosion resistance is lowered and the solderability is lowered, so that the brazing property is lowered. Therefore, when making a core material contain Cu, content of Cu is 3.0 mass% or less.
  • the core material Fe improves strength by solid solution strengthening action. However, when the content of Fe exceeds 1.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound. Therefore, when the core material contains Fe, the content of Fe is 1.5% by mass or less.
  • Ti 0.5 mass% or less of core material
  • the core material Ti nobles the potential of the core material and improves the corrosion resistance.
  • content of Ti exceeds 0.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound. Therefore, when making a core material contain Ti, content of Ti is 0.5 mass% or less.
  • the core material Cr forms dispersed particles of Al-Cr system to improve the strength of the core material.
  • content of Cr exceeds 0.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound. Therefore, when making a core material contain Cr, content of Cr is 0.5 mass% or less.
  • the core material Zr forms dispersed particles of Al-Zr system to improve the strength of the core material.
  • the content of Zr exceeds 0.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound. Therefore, when the core material contains Zr, the content of Zr is 0.5% by mass or less.
  • the core material Ti, Cr, and Zr if not exceeding the upper limit described above, not only when the core material contains one or more types, that is, when one type is included, but two or more types are included in the present invention Do not disturb the effect.
  • Li of core material 0.3 mass% or less
  • Heartwood Li further improves the brazeability.
  • the gettering action of Mg is achieved by the destruction of the oxide film formed on the surface of the brazing material during the brazing heat when the brazing heat is applied. It is speculated that it should be made more effective.
  • the content of Li exceeds 0.3% by mass, Li diffuses into the surface layer of the brazing material in the temperature rising process during brazing heating to promote the growth of the oxide film, and the brazing property decreases. Therefore, when the core material contains Li, the content of Li is 0.3% by mass or less.
  • the content of Li in the core material is preferably 0.05% by mass or less.
  • the balance of the core material is preferably Al and unavoidable impurities.
  • V, Ni, Ca, Na, Sr, etc. may be mentioned, and these elements may be contained in the range which does not disturb the effect of the present invention. Specifically, V: 0.05% by mass or less, Ni: 0.05% by mass or less, Ca: 0.05% by mass or less, Na: 0.05% by mass or less, Sr: 0.05% by mass or less, and the like
  • the element of: may be contained in a range of less than 0.01% by mass.
  • the brazing material of the brazing sheet according to the present embodiment is made of an aluminum alloy, and more specifically, made of an aluminum alloy containing Si, Bi, and Mg.
  • aluminum alloys JIS-4000 Al-Si alloys (Al-Si-Mg-Bi alloys), Al-Si-Zn alloys (Al-Si-Zn-Mg-Bi alloys), etc. Can be used.
  • the brazing material of the brazing sheet according to the present embodiment may further contain Mn, Ti, Cr, Zr, Zn, Sr, Na, Sb, a rare earth element, and Li as appropriate.
  • the brazing material Si improves the liquid phase rate at the brazing heat addition temperature and enhances the fluidity of the brazing material.
  • the content of Si is 3% by mass or more, the fluidity of the braze is enhanced, and the effect of improving the brazeability can be obtained.
  • the content of Si exceeds 13% by mass, coarse Si particles are formed, and excessive flow solder is generated, which may cause brazing failure such as melting of the core material. Therefore, the content of Si in the brazing material is 3% by mass or more and 13% by mass or less.
  • the content of Si in the brazing material is C Si mass%, 3 ⁇ C Si ⁇ 13.
  • the brazing material Bi reacts with the core material and the brazing material Mg to form a Mg—Bi-based compound (eg, Bi 2 Mg 3 ) which hardly dissolves below the brazing material melting temperature.
  • a Mg—Bi-based compound eg, Bi 2 Mg 3
  • the diffusion of Mg to the brazing filler metal surface layer is suppressed, and the formation and growth of MgO on the brazing filler metal surface are suppressed ( Mg trapping effect), improve the brazeability.
  • the content of Bi in the brazing material needs to be very precisely specified in relation to the content of Mg in the core material and the brazing material.
  • the content of Mg in the brazing material is CMg-b mass%
  • the content of Mg in the core material is CMg-c mass%
  • CMg CMg-b + CMg-c / 2
  • the content of Bi in the brazing material is less than 0.13 C Mg -0.3 , Mg can not be trapped sufficiently and, as a result, free Mg is increased in the brazing material, so that MgO is generated on the surface of the brazing material.
  • the content of Bi in the brazing material 0.13C Mg -0.3 or more, 0.58C Mg 0.45 or less. Then, when the content of Bi in the brazing material and C Bi mass%, 0.13C Mg -0.3 ⁇ C Bi ⁇ 0.58C Mg 0.45.
  • the brazing material Mg evaporates into the atmosphere at the brazing material melting temperature at the time of heat addition, and reacts with oxygen in the atmosphere.
  • the oxide film formed on the surface of the brazing material is suitably destroyed at the time of evaporation of Mg, and the oxygen concentration in the atmosphere is lowered to suppress reoxidation of molten brazing (getter action).
  • Mg of the core material also exerts a getter action, when the content of Mg of the core material is large, the content of Mg of the brazing material may be small.
  • the content of Mg in the brazing material is 0.1% by mass or more.
  • Mg of brazing material and Mg of core material 0.2 ⁇ C Mg ⁇ 1.1
  • Mg of the brazing material and Mg of the core material both improve the brazeability by exerting a getter function.
  • the contribution to the gettering action differs between Mg of the brazing material and Mg of the core material, so in order to properly exhibit the effect of improving the brazeability based on the gettering action, the Mg of the brazing material and the core material It is necessary to precisely specify the content of Mg and Mg.
  • C Mg is preferably 0.3 or more.
  • C Mg is preferably 0.9 or less.
  • Mn of brazing material 2.0% by mass or less
  • the brazing material Mn improves the corrosion resistance.
  • Al-Mn-Si compounds are formed, and Mn and Si-depleted layers around the compound become potential dark areas, and corrosion progresses preferentially Therefore, it is presumed that the corrosion is dispersed and the corrosion resistance is improved.
  • Si is consumed for the formation of an Al-Mn-Si-based compound, so that the Si concentration is lowered and the brazing property is lowered. Therefore, when the brazing material contains Mn, the content of Mn in the brazing material is 2.0% by mass or less.
  • the content of Mn of a brazing filler material is preferably 1.2% by mass or less.
  • the brazing material Ti improves the corrosion resistance. Although the detailed mechanism by which Ti improves the corrosion resistance has not been elucidated, Al-Ti based compounds are formed, and the Ti-depleted layer around the compound becomes a shallow part of the potential, and the corrosion progresses preferentially, so the corrosion It is estimated that it is dispersed and the corrosion resistance is improved. However, if the content of Ti exceeds 0.3% by mass, coarse compounds are generated during melting and casting, and cracking tends to occur during material production, making production difficult. Therefore, when the brazing material contains Ti, the content of Ti in the brazing material is 0.3% by mass or less.
  • the content of Ti in the brazing material is preferably 0.2% by mass or less.
  • the brazing filler metal Cr improves the corrosion resistance. Although the detailed mechanism by which Cr improves the corrosion resistance has not been elucidated, Al-Cr and Al-Cr-Si compounds are formed, and the Cr and Si-depleted layer around the compound becomes a subtle part of the potential, which is preferred. It is assumed that the corrosion progresses and the corrosion is dispersed and the corrosion resistance is improved. However, if the content of Cr exceeds 0.3% by mass, coarse compounds are generated during melting and casting, and cracking tends to occur during material production, making production difficult. Therefore, when the brazing material contains Cr, the content of Cr in the brazing material is 0.3% by mass or less.
  • the content of Cr in the brazing material is preferably 0.2% by mass or less.
  • the brazing material Zr improves the corrosion resistance. Although the detailed mechanism by which Zr improves the corrosion resistance has not been elucidated, Al-Zr based compounds are formed, and the Zr-depleted layer around the compound becomes a subtle part of the potential, and the corrosion progresses preferentially, so the corrosion is It is estimated that it is dispersed and the corrosion resistance is improved. However, if the content of Zr exceeds 0.3% by mass, coarse compounds are generated during melting and casting, and cracking tends to occur during material production, making production difficult. Therefore, when the brazing material contains Zr, the content of Zr in the brazing material is 0.3% by mass or less.
  • the content of Zr of a brazing material is preferably 0.2% by mass or less.
  • Mn, Ti, Cr, and Zr of the above-mentioned brazing material are not limited to the case where the brazing material contains one or more kinds, that is, one or two kinds. , Does not interfere with the effects of the present invention.
  • Zn of brazing material 5.0% by mass or less
  • Zn of the brazing material can make the potential of the brazing material more strong, and by forming a potential difference with the core material, the corrosion resistance is improved by the sacrificial anticorrosion effect.
  • the content of Zn exceeds 5.0% by mass, premature fillet corrosion may occur. Therefore, when the brazing material contains Zn, the content of Zn in the brazing material is 5.0% by mass or less.
  • the content of Zn of a brazing material is preferably 4.0 mass% or less.
  • the brazing material Sr suppresses crystallization of coarse Si particles which causes melting of the core material at the time of heat addition to a brazing material by refining eutectic Si. However, if the content of Sr exceeds 0.10% by mass, the flowability of the wax may be reduced, and the formation of fillets may be insufficient at the time of heat addition to the wax. Therefore, when the brazing material contains Sr, the content of Sr is 0.10 mass% or less.
  • content of Sr of a brazing material has preferable 0.001 mass% or more.
  • the brazing material Na suppresses crystallization of coarse Si particles that causes melting of the core material at the time of heat addition to the brazing material.
  • the content of Na exceeds 0.050% by mass, the flowability of the wax may be reduced, and the formation of fillets may be insufficient at the time of heat addition to the wax. Therefore, when the brazing material contains Na, the content of Na is 0.050% by mass or less.
  • the brazing material Sb suppresses the crystallization of coarse Si particles, which causes melting of the core material at the time of heat addition, by refining eutectic Si. However, if the content of Sb exceeds 0.5% by mass, the fluidity of the wax may be reduced, and the formation of fillets may be insufficient at the time of heat addition to the wax. Therefore, when the brazing material contains Sb, the content of Sb is 0.5% by mass or less.
  • the brazing material is not limited to one or more kinds, that is, one or two kinds. It does not disturb the effect of the invention.
  • the rare earth element is a generic term of 17 elements of the 3rd group of the periodic table obtained by adding a lanthanoid (15 elements) to Sc and Y, and examples thereof include Sc, Y, La, Ce, Nd and Dy. And when making a brazing material contain a rare earth element, even if it contains 1 type, 2 or more types may be contained.
  • the method of containing the rare earth element in the brazing material is not particularly limited, two or more kinds of the rare earth elements can be simultaneously contained by, for example, addition of an Al-rare earth intermediate alloy or addition of misch metal.
  • the rare earth element of the brazing material reacts with the surface oxide film (Al 2 O 3 ) of the brazing material and the rare earth element or the oxide containing the rare earth element during heat addition of the brazing material to cause volume contraction of the surface oxide film of the brazing material. Improves the solderability because it destroys the oxide film. However, if the content of the rare earth elements (total amount when two or more are contained) exceeds 1.0% by mass, an oxide film containing the rare earth elements is excessively generated, and the effect of the oxide film destruction is reduced. Brazeability is reduced. Therefore, when the brazing material contains a rare earth element, the content of the rare earth element in the brazing material is 1.0% by mass or less.
  • the content of the rare earth element of the brazing material is preferably 0.001% by mass or more in order to further ensure the effect of the oxide film destruction obtained by containing the rare earth element.
  • the brazing material Li like the core material Li, further improves the brazeability.
  • the gettering action of Mg is achieved by the destruction of the oxide film formed on the surface of the brazing material during the brazing heat when the brazing heat is applied. It is speculated that it should be made more effective.
  • the content of Li exceeds 0.3% by mass, Li promotes the growth of the oxide film, and the brazing property is reduced. Therefore, when the brazing material contains Li, the content of Li is 0.3% by mass or less.
  • the content of Li in the brazing material is preferably 0.05% by mass or less.
  • the balance of the brazing material is preferably Al and unavoidable impurities.
  • Fe, Ca, Be, etc. may be contained in the range which does not disturb the effect of the present invention.
  • other elements: less than 0.01% by mass may be contained.
  • Ru if it does not exceed the above-mentioned predetermined content, not only when it is contained as an unavoidable impurity but also when it is added positively, it is acceptable without disturbing the effect of the present invention Ru.
  • Mn, Ti, Cr, Zr, Zn, Sr, Na, Sb, rare earth elements, and Li may be added actively, you may contain as an unavoidable impurity.
  • the thickness of the brazing sheet according to the present embodiment is not particularly limited, but when used for a tube material, it is preferably 0.5 mm or less, more preferably 0.4 mm or less, and 0.05 mm or more. Is preferred. And when using for a side support material, a header material, and a tank material, as for the thickness of the brazing sheet which concerns on this embodiment, 2.0 mm or less is preferable, 1.5 mm or less is more preferable, and 0.5 mm or more Is preferred. Moreover, when using for a fin material, the thickness of the brazing sheet according to the present embodiment is preferably 0.2 mm or less, more preferably 0.15 mm or less, and 0.01 mm or more. Is preferred. In addition, the thickness of the brazing sheet according to the present embodiment is particularly preferably 0.5 mm or more based on the viewpoint of securing an appropriate thickness of the brazing material without impairing basic characteristics such as strength after brazing.
  • the thickness of the brazing material of the brazing sheet according to the present embodiment is not particularly limited when applied to any plate material, 2 ⁇ m or more is preferable, and 50 ⁇ m or more is more preferable. By setting the thickness of the brazing material to a predetermined value or more, the absolute amount of Mg contained in the brazing material increases, and the getter effect can be more reliably exhibited.
  • the thickness of the brazing material is preferably 250 ⁇ m or less.
  • the clad ratio of the brazing material of the brazing sheet according to the present embodiment is not particularly limited when applied to any plate material, 40% or less is preferable, and 30% or less is more preferable. By making the cladding ratio of the brazing material equal to or less than a predetermined value, it is possible to avoid or suppress deterioration of basic characteristics such as strength after brazing and productivity.
  • the brazing sheet according to the present embodiment has been described by exemplifying the configuration of the two-layer structure shown in FIG. 1, the other configurations are not excluded.
  • the configuration of the brazing sheet according to the present embodiment is a sacrificial material (sacrificial material) on the other side of the core 2 shown in FIG. 1 (the side opposite to the side on which the brazing material 3 is provided) according to the user's request.
  • An anticorrosive material, a sacrificial material) or an intermediate material may be provided.
  • a brazing material may be further provided on the other side of the core material 2.
  • the brazing sheet according to the present embodiment is provided with brazing materials on both sides of the core material, if any one of the brazing materials satisfies the invention specific matters of the present invention, the other brazing material of the present invention It may be a brazing material which does not satisfy the invention specific matters (for example, an Al-Si alloy such as JIS 4045, 4047, 4343, an Al-Si-Zn alloy, an Al-Si-Mg alloy, etc.).
  • flux may be applied to the surface of the brazing material and brazing may be performed.
  • Any sacrificial material may be used as long as it has a known component composition capable of exhibiting the sacrificial corrosion preventing ability, and, for example, JIS 1000 pure aluminum and JIS 7000 Al-Zn alloy can be used. Moreover, various aluminum alloys can be used as an intermediate material according to the required characteristics. In addition, the alloy number shown to this specification is based on JIS H 4000: 2014 and JIS Z 3263: 2002.
  • the brazing sheet according to the present embodiment is excellent in corrosion resistance because the components and contents of the core material and the brazing material are specified. Therefore, according to the brazing sheet according to the present embodiment, the structure after brazing can correspond to various usage environments and atmospheres.
  • the manufacturing method of the brazing sheet which concerns on this embodiment is not specifically limited, For example, it manufactures by the manufacturing method of a well-known clad material. An example will be described below. First, melt and cast an aluminum alloy of each composition of core material and brazing material, and if necessary, carry out facing (surface smoothing treatment of ingot) and homogenization treatment, and then give each ingot obtain. Then, the ingot of the brazing material is hot-rolled to a predetermined thickness, combined with the ingot of the core material, and made into a clad material by hot-rolling according to a conventional method.
  • the clad material is subjected to cold rolling, intermediate annealing if necessary, and final cold rolling, and final annealing if necessary.
  • the homogenization treatment is preferably performed at 400 to 600 ° C. for 1 to 20 hours, and the intermediate annealing is preferably performed at 300 to 450 ° C. for 1 to 20 hours.
  • final annealing is preferably performed at 150 to 450 ° C. for 1 to 20 hours.
  • the tempering may be any of H1 n, H2 n, H3 n and O (JIS H 0001: 1998).
  • the manufacturing method of the aluminum alloy brazing sheet according to the present embodiment is as described above, but in each of the steps, the conventionally known conditions may be used for the conditions that are not specified, and the treatment in each of the steps is described. It is needless to say that the conditions can be appropriately changed as long as the effects obtained by
  • the brazing method of the aluminum alloy brazing sheet according to the present embodiment is so-called fluxless brazing which does not use a flux, and is a method of heating under a predetermined heating condition in an inert gas atmosphere.
  • Heating condition Heating rate
  • the temperature rising rate from 350 ° C. to 560 ° C. is preferably 1 ° C./min or more and 500 ° C./min or less.
  • the temperature rising rate from 350 ° C. to 560 ° C. is preferably 10 ° C./min or more.
  • the temperature rising rate from 350 ° C. to 560 ° C. is preferably 300 ° C./min or less.
  • the temperature lowering rate from 560 ° C. is not particularly limited, and may be, for example, 5 ° C./min or more and 1000 ° C./min or less.
  • the heating rate from 560 ° C. to the actual heating temperature is not particularly limited, the heating rate within the same range as the heating rate from 350 ° C. to 560 ° C. do it.
  • the temperature decrease rate from the actual heating temperature to 560 ° C. is not particularly limited, it may be a rate within the same range as the temperature decrease rate from 560 ° C.
  • the heating temperature (brazing melting temperature) when heating the brazing sheet according to the present embodiment is 560 ° C. or more and 620 ° C. or less at which the brazing material is appropriately melted, and is preferably 580 ° C. or more and 620 ° C. or less. And if the holding time in this temperature range is less than 10 seconds, the time required for the occurrence of brazing phenomenon (destruction of oxide film, reduction of oxygen concentration in the atmosphere, flow of molten solder to the joint) is insufficient there's a possibility that. Therefore, the holding time in a temperature range of 560 ° C. to 620 ° C. (preferably a temperature range of 580 ° C. to 620 ° C.) is preferably 10 seconds or more.
  • the holding time in a temperature range of 560 ° C. or more and 620 ° C. is preferably 30 seconds or more and 60 seconds or more. More preferable.
  • the upper limit of the holding time is not particularly limited, it may be 1500 seconds or less.
  • the atmosphere at the time of heating (brazing) the brazing sheet according to the present embodiment is an inert gas atmosphere, for example, a nitrogen gas atmosphere, an argon gas atmosphere, a helium gas atmosphere, or a mixed gas atmosphere in which a plurality of these gases are mixed. It is.
  • the inert gas atmosphere is preferably an atmosphere having as low an oxygen concentration as possible. Specifically, the oxygen concentration is preferably 50 ppm or less, more preferably 10 ppm or less.
  • the brazing method of the aluminum alloy brazing sheet which concerns on this embodiment does not need to evacuate an atmosphere, and can be performed by a normal pressure (atmospheric pressure).
  • the member to be joined is assembled so as to be in contact with the brazing material of the brazing sheet (assembly step) .
  • the brazing sheet may be formed into a desired shape and structure before the assembling step (forming step).
  • the brazing method of the brazing sheet according to the present embodiment (in other words, the method of manufacturing a structure in which the member to be joined is brazed to the brazing sheet) is as described above. Needless to say, conventionally known conditions may be used, and the conditions can be appropriately changed as long as the effects obtained by the treatment can be obtained.
  • the brazing method of the brazing sheet according to the present embodiment exhibits excellent corrosion resistance because the components and the contents of the core material and brazing material of the brazing sheet to be used are specified. Therefore, according to the brazing method of the brazing sheet according to the present embodiment, the structure after brazing can correspond to various usage environments and atmospheres.
  • the method of manufacturing a heat exchanger according to the present embodiment is a method including a brazing step of performing the above-described brazing method.
  • each process other than the brazing process for example, the forming process and the assembling process described above may be performed by a conventionally known method.
  • Example material preparation The core material of the composition shown in Table 1 was casted, subjected to homogenization treatment at 500 ° C. for 10 hours, and chamfered on both sides to a predetermined thickness. Further, a brazing material having a composition shown in Table 2 was cast, homogenized at 500 ° C. for 10 hours, subjected to hot rolling to a predetermined thickness, and a hot-rolled sheet was produced. Then, the core material and the brazing material were combined and subjected to hot rolling to obtain a clad material. Thereafter, cold rolling is performed to obtain a thickness of 0.4 mm (the clad ratio of the brazing material is 10%), final annealing at 400 ° C.
  • test material A65 and A66 it was set as the thickness different from the thickness mentioned above (The thickness of test material A65 is 0.6 mm, the clad ratio of brazing material is 10%, the thickness of test material A66 is The clad ratio of the brazing material was 0.8%, and the other preparation conditions were the same.
  • brazing equivalent heating The brazing equivalent heating was performed in a nitrogen atmosphere with an oxygen concentration of 10 ppm under the conditions of a temperature rising rate of 30 ° C./min from 350 to 560 ° C. and a holding time of 180 s in the 580 to 620 ° C. range.
  • the test materials shown in Table 4 carried out brazing equivalent heating under the conditions described in the table.
  • the temperature rising rate from 560 ° C. to the highest achieved temperature was the same as the temperature rising rate from 350 ° C. to 560 ° C., and the temperature lowering rate was 100 ° C./min.
  • a fixed clearance was set by sandwiching the stainless steel spacer 12 of ⁇ 2 mm between the upper plate 11 (the test piece (vertical width 25 mm ⁇ horizontal width 55 mm)) disposed.
  • the upper plate 11 was fixed by the wire 13.
  • symbol 14 in FIG. 2B is a "fillet.” And it joined by brazing on the conditions of the above-mentioned brazing equivalent heating. After brazing and bonding, the brazeability was quantified by measuring a length L (gap filling length) in which the gap between the lower and upper plates was filled.
  • this brazing property is the gap filling property, and is caused by the occurrence of thermal deformation of the brazing sheet and the members to be joined at the time of brazing, which are generated when the members are assembled. It is brazability which considered the crevice between member joint surfaces which arises.
  • those with a gap filling length of 45 mm or more are “ ⁇ ”
  • those with 35 mm or more and less than 45 mm are “ ⁇ ”
  • those with 25 mm or more and less than 35 mm are “O”
  • those with 15 mm or more and less than 25 mm ⁇ ” were evaluated as "x”
  • " ⁇ ", " ⁇ ", " ⁇ ", and “ ⁇ ” were evaluated as pass and "x" was evaluated as failure.
  • this immersion test heats OY water from room temperature to 88 ° C. in 1 hour and holds it at this 88 ° C. for 7 hours, then cools to room temperature in 1 hour and holds it at this room temperature for 15 hours A series of flow was made one cycle a day, and it was to be performed for 20 days. After the immersion test, even in the test surface, the area where corrosion is most prominent was observed with an optical microscope to determine the corrosion form and the corrosion depth.
  • Table 1 shows the composition of the core material
  • Table 2 shows the composition of the brazing material
  • Table 3 shows the composition of the test material
  • the evaluation result shows the composition of the test material, brazing The conditions and the evaluation results are shown.
  • the core material of Table 1 and the remaining part of the brazing material of Table 2 are Al and unavoidable impurities, and "-" in the table indicates that it does not contain (is below the detection limit).
  • the values of “0.13 C Mg ⁇ 0.3 ” and “0.58 C Mg 0.45 ” shown in Table 3 are values rounded to the third decimal place.
  • test materials A1 to A66 and B1 to B8 satisfied the requirements defined by the present invention. Therefore, the test materials A1 to A66 and B1 to B8 resulted in "Brazing property” to pass, and the test materials A1 to A66 resulted in "Corrosion resistance” also to pass.
  • C Bi 0.13C Mg -0.3 in Fig 3
  • test materials A100 to A114 did not satisfy the requirements defined by the present invention, and as a result, the result was that the brazing property failed or that edge cracking occurred during hot rolling.
  • the details are as follows.
  • the test material A100 has a large value of C 2 Mg , and the generation of MgO on the surface of the brazing material is promoted, and as a result, the brazing property becomes “x”.
  • the test material A101 has a large value of C 2 Bi , and that the oxide film based on the Bi simplex compound has suppressed the gettering action, and further, the value of C 2 Mg is small and the gettering action is insufficient As a result, the brazability became "x”.
  • the test material A102 has a small value of C 2 Bi and can not sufficiently trap Mg, thereby promoting the formation of MgO on the surface of the brazing material. As a result, the brazing property is “ It became "x”.
  • the test material A103 has a small value of C 2 Bi and can not sufficiently trap Mg, thereby promoting the formation of MgO on the surface of the brazing material.
  • the brazing property is “ It became "x”.
  • the test material A104 has a small value of C 2 Bi and can not trap Mg sufficiently, thereby promoting the formation of MgO on the surface of the brazing material, and as a result, the brazing property is “ It became "x”.
  • the test material A105 has a large value of C 2 Bi , and the oxide film based on the Bi simplex compound has suppressed the getter action, and as a result, the brazing property becomes “x”.
  • test material A106 has a large value of C 2 Bi , and the oxide film based on the Bi simplex compound has suppressed the getter action, and as a result, the brazing property becomes “x”.
  • test material A107 has a large value of C 2 Bi , and the oxide film based on the Bi simplex compound has suppressed the getter action, and as a result, the brazing property becomes “x”.
  • sample material A108 has a small value of C 2 Bi and can not sufficiently trap Mg, thereby promoting the formation of MgO on the surface of the brazing material. As a result, the brazing property is “ ⁇ It became ".
  • sample material A109 has a small value of C 2 Bi and can not trap Mg sufficiently and that the generation of MgO on the surface of the brazing material is promoted, and further, the value of C 2 Mg is small It was assumed that the gettering action was insufficient, and as a result, the brazeability was "x". It is assumed that the test material A110 has a small value of C Bi and can not sufficiently trap Mg, and the generation of MgO on the surface of the brazing material is promoted, and as a result, the brazing property is “ It became "x”.
  • the sample material A111 had a large value of C 2 Mg , and was assumed to promote the formation of MgO on the surface of the brazing material, and as a result, the brazing property became “x”.
  • the sample material A112 is assumed to have a small value of C 2 Bi and to be unable to trap Mg sufficiently and to promote the formation of MgO on the surface of the brazing material. Furthermore, the value of C 2 Mg is large. It was assumed that the formation of MgO on the surface of the brazing material was promoted, and as a result, the brazing property became “x”.
  • test material A113 has a large value of C 2 Bi
  • oxide film based on the Bi simplex compound has suppressed the gettering action, and further, the value of C 2 Mg is small and the gettering action is insufficient As a result, the brazability became "x".
  • the sample material A114 has a small value of CMg-b , and it is assumed that the Bi simplex compound melts during hot rolling and induces hot rolling cracking (ear crack).
  • the method of the present invention it is possible to improve the brazeability of fluxless brazing in an inert gas atmosphere which is not a vacuum, and is particularly useful for the production of a heat exchanger.

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Abstract

Provided is a brazing method for an aluminum alloy brazing sheet provided with a core material and a brazing material in which the Si content of the brazing material is denoted by CSi, the Bi content of the brazing material is denoted by CBi, the Mg content of the brazing material is denoted by CMg-b, the Mg content of the core material is denoted by CMg-c, CMg = CMg-b + CMg-c / 2, and an aluminum alloy brazing sheet satisfying 3 ≤ CSi ≤ 13, 0.13CMg -0.3 ≤ CBi ≤ 0.58CMg 0.45, CMg-b ≥ 0.1, and 0.2 ≤ CMg ≤ 1.1 is brazed in an inert gas atmosphere at a heating temperature of 560-620 °C without using flux.

Description

アルミニウム合金ブレージングシートのろう付方法、及び、熱交換器の製造方法Method of brazing aluminum alloy brazing sheet and method of manufacturing heat exchanger
　本発明は、アルミニウム合金ブレージングシートのろう付方法、及び、熱交換器の製造方法に関し、特に、フラックスを使用しないろう付方法、いわゆるフラックスレスろう付方法、及び、フラックスレスろう付方法を用いた熱交換器の製造方法に関する。 The present invention relates to a method of brazing an aluminum alloy brazing sheet and a method of manufacturing a heat exchanger, and in particular, a flux-free brazing method, a so-called fluxless brazing method, and a fluxless brazing method The present invention relates to a method of manufacturing a heat exchanger.
　アルミニウム合金製の熱交換器等の部材をろう付するにあたり、真空中において、フラックスを使用せずにろう付を行う真空ろう付という方法が存在する。
　この真空ろう付は、フラックスを使用するフラックスろう付と比較すると、フラックスを塗布する処理が不要、フラックスの塗布量が適切でないことに伴った問題発生の回避等、様々なメリットがある。 In brazing members such as aluminum alloy heat exchangers, there is a method called vacuum brazing in which brazing is performed without using flux in a vacuum.
This vacuum brazing has various merits such as the necessity of the process of applying the flux and the avoidance of the problem caused by the inappropriate application amount of the flux as compared with the flux brazing using the flux.
　しかしながら、真空ろう付は、ろう付時の炉内を真空にした状態で加熱を施す高価な真空炉が必要となるため、作業コストが高くなってしまうとともに、真空にした炉内の制御が難しいことから、作業の困難性も高まってしまう。 However, vacuum brazing requires an expensive vacuum furnace to heat the furnace in a vacuumed state at the time of brazing, which increases the operation cost and makes it difficult to control the vacuumed furnace. This makes the work more difficult.
　このような問題を解決するため、真空中ではない雰囲気下において、フラックスを使用しないフラックスレスろう付に関して研究が進められ、以下のような技術が提案されている。 In order to solve such problems, research has been conducted on fluxless brazing using no flux under an atmosphere not in vacuum, and the following techniques have been proposed.
　具体的には、特許文献１において、質量％で、Ｍｇを０．１～５．０％、Ｓｉを３～１３％含有するＡｌ－Ｓｉ系ろう材が最表面に位置するアルミニウムクラッド材を用いる細流路インナーフィンを有する熱交換器のろう付け方法であって、前記Ａｌ－Ｓｉ系ろう材に含まれるＳｉ粒子は、円相当径で０．８μｍ以上の径をもつものの数の内、１．７５μｍ以上の径のものの数が２５％以上であり、減圧を伴わない非酸化性雰囲気で、前記Ａｌ－Ｓｉ系ろう材とろう付け対象部材とを接触密着させ、加熱温度５５９～６２０℃において、前記アルミニウムクラッド材と前記ろう付け対象部材とを接合することを特徴とする細流路インナーフィンを有する熱交換器のフラックスレスろう付け方法が開示されている。 Specifically, in Patent Document 1, an aluminum clad material is used in which an Al—Si-based brazing material containing 0.1 to 5.0% of Mg and 3 to 13% of Si by mass% is located on the outermost surface. A method of brazing a heat exchanger having narrow channel inner fins, wherein the Si particles contained in the Al-Si-based brazing material have a circle equivalent diameter of those having a diameter of 0.8 μm or more. The Al-Si-based brazing material is brought into close contact with the brazing target member in a non-oxidizing atmosphere with a pressure of 25% or more and a diameter of 75 μm or more at a heating temperature of 559 to 620 ° C. There is disclosed a fluxless brazing method of a heat exchanger having narrow channel inner fins, characterized in that the aluminum clad material and the brazing target member are joined.
日本国特許第５６１９５３８号公報Japanese Patent No. 5619538
　特許文献１に係る技術は、真空ではない不活性ガス雰囲気におけるフラックスレスろう付に関する技術であり、所定の効果について検討している。
　しかしながら、特許文献１に係る技術では、十分なろう付性を発揮できない。詳細には、特許文献１の実施例１～２３、２９～５８によると、ろう材に０．１～３質量％のＭｇを含有させており、このＭｇがろう付加熱時の昇温過程において、ろう材表面でのＭｇＯの生成を促進させてしまう。その結果、特許文献１の実施例１～２３、２９～５８によると、ろう材表面のＭｇＯがろう溶融時に障害となって、ろう付性を低下させてしまうおそれがある。
　なお、特許文献１の実施例２４～２８ではろう材にＢｉを含有させているが、実施例２４～２６はろう材のＢｉの含有量が少なく、実施例２７、２８はＢｉの含有量が多いため、いずれの場合もろう付性を十分には発揮できない。 The technique according to Patent Document 1 relates to fluxless brazing in an inert gas atmosphere that is not a vacuum, and is examining a predetermined effect.
However, the technology according to Patent Document 1 can not exhibit sufficient brazeability. In detail, according to Examples 1 to 23 and 29 to 58 of Patent Document 1, the brazing material contains 0.1 to 3% by mass of Mg, and this Mg is in the temperature rising process at the time of the brazing addition heat. And promote the formation of MgO on the surface of the brazing material. As a result, according to Examples 1 to 23 and 29 to 58 of Patent Document 1, MgO on the surface of the brazing material may become an obstacle at the time of brazing and melting, and the brazing property may be reduced.
In Examples 24 to 28 of Patent Document 1, Bi is contained in the brazing material, but in Examples 24 to 26, the content of Bi in the brazing material is small, and in Examples 27 and 28, the content of Bi is Since there are many, in any case, it is not possible to fully exhibit brazeability.
　そこで、本発明は、優れたろう付性を発揮することができるアルミニウム合金ブレージングシートのろう付方法、及び、熱交換器の製造方法を提供することを課題とする。 Then, this invention makes it a subject to provide the brazing method of the aluminum alloy brazing sheet which can exhibit the outstanding brazing property, and the manufacturing method of a heat exchanger.
　すなわち、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、心材と、前記心材の一方の面に設けられるろう材と、を備えるアルミニウム合金ブレージングシートのろう付方法であって、前記心材は、Ｍｇ：２．０質量％以下（０質量％を含む）であるアルミニウム合金からなり、前記ろう材は、Ｓｉ、Ｂｉ、Ｍｇを含有するアルミニウム合金からなり、前記ろう材のＳｉの含有量をＣＳｉ質量％とし、前記ろう材のＢｉの含有量をＣＢｉ質量％とし、前記ろう材のＭｇの含有量をＣＭｇ－ｂ質量％とし、前記心材のＭｇの含有量をＣＭｇ－ｃ質量％とし、ＣＭｇ＝ＣＭｇ－ｂ＋ＣＭｇ－ｃ／２とした場合に、３≦ＣＳｉ≦１３、０．１３ＣＭｇ －０．３≦ＣＢｉ≦０．５８ＣＭｇ ０．４５、ＣＭｇ－ｂ≧０．１、０．２≦ＣＭｇ≦１.１、を満たし、前記アルミニウム合金ブレージングシートを不活性ガス雰囲気においてフラックスを用いずに５６０～６２０℃の加熱温度によってろう付する。 That is, a brazing method of an aluminum alloy brazing sheet according to the present invention is a brazing method of an aluminum alloy brazing sheet including a core and a brazing material provided on one surface of the core, wherein the core is Mg: 2.0 mass% or less (including 0 mass%) comprising an aluminum alloy, the brazing material comprising an aluminum alloy containing Si, Bi, and Mg, the Si content of the brazing material being C Si mass%, Bi content of the brazing material is C Bi mass%, Mg content of the brazing material is C Mg-b mass%, Mg content of the core material is C Mg-c mass % and then, C Mg = C Mg-b + C when the Mg-c / 2, 3 ≦ C Si ≦ 13,0.13C Mg -0.3 ≦ C Bi ≦ 0.58C Mg 0.45, C Mg -B ≧ 0 1 and 0.2 ≦ C Mg ≦ 1.1, and the aluminum alloy brazing sheet is brazed at a heating temperature of 560 to 620 ° C. without using a flux in an inert gas atmosphere.
　このように、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、使用するアルミニウム合金ブレージングシートの心材及びろう材の成分の含有量、例えば、心材及びろう材のＭｇの含有量とろう材のＢｉの含有量との関係等が特定されていることから、心材及びろう材のＭｇがろう材のＢｉと反応する（トラップされる）ことで、ろう材表面でのＭｇＯの生成が抑制される。さらに、ろう付加熱時のろう溶融時において、Ｂｉと反応したＭｇは母相（ろう材）に溶解するため、Ｍｇの蒸発が促進され、ろう材表面に形成された酸化膜がＭｇの蒸発時に好適に破壊されるとともに、このＭｇが雰囲気中の酸素と反応することで雰囲気の酸素濃度が低下し溶融ろうの再酸化が抑制される。また、母相に溶解したＢｉがろうの流動性を高める。その結果、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、優れたろう付性を発揮する。 Thus, in the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material of the aluminum alloy brazing sheet used and the content of the components of the brazing material, for example, the Mg content of the core and brazing material and the brazing material Since the relationship with the content of Bi, etc. is specified, the formation of MgO on the surface of the brazing material is suppressed by the reaction (trap) of Mg of the core material and the brazing material with Bi of the brazing material. . In addition, Mg which has reacted with Bi dissolves in the matrix (brazing material) during brazing and melting when brazing is applied heat, so evaporation of Mg is promoted, and the oxide film formed on the brazing material surface is evaporated during Mg evaporation. While being suitably destroyed, the reaction of this Mg with oxygen in the atmosphere lowers the concentration of oxygen in the atmosphere and suppresses reoxidation of the molten wax. In addition, Bi dissolved in the matrix improves the fluidity of the wax. As a result, the method for brazing an aluminum alloy brazing sheet according to the present invention exhibits excellent brazability.
　また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材が、Ｍｎ：２．０質量％以下、Ｔｉ：０．３質量％以下、Ｃｒ：０．３質量％以下、Ｚｒ：０．３質量％以下のうちの１種以上をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材が、Ｚｎ：５．０質量％以下をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材が、Ｓｒ：０．１０質量％以下、Ｎａ：０．０５０質量％以下、Ｓｂ：０．５質量％以下、のうちの１種以上をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材が、希土類元素：１．０質量％以下をさらに含有していてもよい。 Further, in the brazing method of the aluminum alloy brazing sheet according to the present invention, the brazing material is Mn: 2.0 mass% or less, Ti: 0.3 mass% or less, Cr: 0.3 mass% or less, Zr: You may further contain 1 or more types in 0.3 mass% or less. In the brazing method of the aluminum alloy brazing sheet according to the present invention, the brazing material may further contain Zn: 5.0% by mass or less. Further, in the brazing method of the aluminum alloy brazing sheet according to the present invention, among the brazing materials, Sr: 0.10 mass% or less, Na: 0.050 mass% or less, Sb: 0.5 mass% or less It may further contain one or more of In the brazing method of the aluminum alloy brazing sheet according to the present invention, the brazing material may further contain rare earth element: 1.0% by mass or less.
　このように、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、ろう材がＭｎ、Ｔｉ、Ｃｒ、Ｚｒ、Ｚｎ、Ｓｒ、Ｎａ、Ｓｂ、希土類元素を含有していても、優れたろう付性を発揮することができる。 Thus, the brazing method of the aluminum alloy brazing sheet according to the present invention is excellent in brazeability even if the brazing material contains Mn, Ti, Cr, Zr, Zn, Sr, Na, Sb, and a rare earth element. Can be demonstrated.
　また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材が、Ｌｉ：０．３質量％以下をさらに含有していてもよい。 In the brazing method of the aluminum alloy brazing sheet according to the present invention, the brazing material may further contain 0.3 mass% or less of Li.
　このように、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材がＬｉを含有することにより、ろう付性をさらに向上させることができる。 Thus, the brazing method of the aluminum alloy brazing sheet according to the present invention can further improve the brazing property because the brazing material contains Li.
　また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材が、Ｍｎ：２．５質量％以下をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材が、Ｓｉ：１．２質量％以下をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材が、Ｃｕ：３．０質量％以下をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材が、Ｆｅ：１．５質量％以下をさらに含有していてもよい。また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材が、Ｔｉ：０．５質量％以下、Ｃｒ：０．５質量％以下、Ｚｒ：０．５質量％以下の１種以上をさらに含有していてもよい。 In the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material may further contain Mn: 2.5% by mass or less. In the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material may further contain Si: 1.2% by mass or less. In the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material may further contain Cu: 3.0 mass% or less. In the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material may further contain Fe: 1.5% by mass or less. In the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material is at least one of Ti: 0.5% by mass or less, Cr: 0.5% by mass or less, and Zr: 0.5% by mass or less May further be contained.
　このように、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、心材がＭｎ、Ｓｉ、Ｃｕ、Ｆｅ、Ｔｉ、Ｃｒ、Ｚｒを含有していても、優れたろう付性を発揮することができる。 Thus, the brazing method for an aluminum alloy brazing sheet according to the present invention can exhibit excellent brazing properties even if the core material contains Mn, Si, Cu, Fe, Ti, Cr, or Zr. .
　また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材が、Ｌｉ：０．３質量％以下をさらに含有していてもよい。 In the brazing method of the aluminum alloy brazing sheet according to the present invention, the core material may further contain 0.3 mass% or less of Li.
　このように、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記心材がＬｉを含有することにより、ろう付性をさらに向上させることができる。 Thus, the brazing method of the aluminum alloy brazing sheet according to the present invention can further improve the brazing property because the core material contains Li.
　また、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、前記ろう材の厚さが５０μｍ以上であってもよい。
　このように、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、ろう材の厚さが所定値以上であることにより、優れたろう付性をより確実に発揮することができる。 In the brazing method of the aluminum alloy brazing sheet according to the present invention, the thickness of the brazing material may be 50 μm or more.
As described above, the brazing method of the aluminum alloy brazing sheet according to the present invention can more reliably exhibit excellent brazing property because the thickness of the brazing material is a predetermined value or more.
　本発明に係る熱交換器の製造方法は、前記したろう付方法を実施するろう付工程を含む。
　このように、本発明に係る熱交換器の製造方法は、所定のろう付方法を実施するろう付工程を含むことにより、優れたろう付性を発揮させつつ熱交換器を製造することができる。 A method of manufacturing a heat exchanger according to the present invention includes a brazing step of performing the above-described brazing method.
Thus, the manufacturing method of the heat exchanger which concerns on this invention can manufacture a heat exchanger, exhibiting excellent brazability by including the brazing process which implements a predetermined | prescribed brazing method.
　本発明に係るアルミニウム合金ブレージングシートのろう付方法は、使用するアルミニウム合金ブレージングシートの心材及びろう材の各成分の含有量が特定されていることによって、優れたろう付性を発揮することができる。
　本発明に係る熱交換器の製造方法は、使用するアルミニウム合金ブレージングシートの心材及びろう材の各成分の含有量が特定されていることによって、優れたろう付性を発揮させつつ熱交換器を製造することができる。 The brazing method of the aluminum alloy brazing sheet according to the present invention can exhibit excellent brazing properties by specifying the contents of the respective components of the core material and the brazing material of the aluminum alloy brazing sheet to be used.
The manufacturing method of the heat exchanger according to the present invention manufactures a heat exchanger while exhibiting excellent brazing property because the content of each component of the core material and brazing material of the aluminum alloy brazing sheet to be used is specified. can do.
本実施形態に係るアルミニウム合金ブレージングシートの断面図である。It is a sectional view of an aluminum alloy brazing sheet concerning this embodiment. ろう付性評価の試験方法を説明するための図であり、下材と上材とを組み合わせた状態の斜視図である。It is a figure for demonstrating the test method of brazing property evaluation, and is a perspective view of the state which combined the lower material and the upper material. ろう付性評価の試験方法を説明するための図であり、下材と上材とを組み合わせた状態の側面図である。It is a figure for demonstrating the test method of brazing property evaluation, and is a side view of the state which combined the lower material and the upper material. 一部の実施例について、ろう材のＢｉの含有量とろう材及び心材のＭｇの含有量との関係を示すグラフである。It is a graph which shows the relationship between the content of Bi of the brazing material and the content of Mg of the brazing material and the core material for some examples. 一部の実施例について、ろう材のＭｇの含有量と心材のＭｇの含有量との関係を示すグラフである。It is a graph which shows the relationship between the content of Mg of the brazing material and the content of Mg of the core material for some examples.
　以下、適宜図面を参照して、本発明に係るアルミニウム合金ブレージングシートのろう付方法、及び、熱交換器の製造方法を実施するための形態（実施形態）について説明する。 Hereinafter, with reference to the drawings as appropriate, a method (aspect) for carrying out a method of brazing an aluminum alloy brazing sheet according to the present invention and a method of manufacturing a heat exchanger will be described.
　まずは、本実施形態に係るアルミニウム合金ブレージングシートのろう付方法（以下、適宜「ろう付方法」という）に使用するアルミニウム合金ブレージングシート（以下、適宜「ブレージングシート」という）について説明する。 First, an aluminum alloy brazing sheet (hereinafter, appropriately referred to as a “brazing sheet”) used for a method of brazing an aluminum alloy brazing sheet according to the present embodiment (hereinafter, appropriately referred to as “brazing method”) will be described.
［アルミニウム合金ブレージングシート］
　本実施形態に係るブレージングシートの構成は、例えば、図１に示すように、心材２と、心材２の一方の面に設けられるろう材３と、を備える。
　そして、本実施形態に係るブレージングシート１は、心材２、ろう材３の各成分の含有量が適宜特定されている。
　以下、本実施形態に係るブレージングシートの心材及びろう材の各成分について数値限定した理由を詳細に説明する。 [Aluminum alloy brazing sheet]
The configuration of the brazing sheet according to the present embodiment includes, for example, as shown in FIG. 1, a core material 2 and a brazing material 3 provided on one surface of the core material 2.
And as for the brazing sheet 1 which concerns on this embodiment, content of each component of the core material 2 and the brazing material 3 is specified suitably.
Hereinafter, the reasons for numerical limitation of each component of the core and brazing material of the brazing sheet according to the present embodiment will be described in detail.
［心材］
　本実施形態に係るブレージングシートの心材は、アルミニウム合金（純アルミニウムも含む）からなり、詳細には、Ｍｇ：２．０質量％以下（０質量％を含む）であるアルミニウム合金からなる。このようなアルミニウム合金としては、ＪＩＳ　２０００系のＡｌ－Ｃｕ系合金、ＪＩＳ　３０００系のＡｌ－Ｍｎ系合金、ＪＩＳ　５０００系のＡｌ－Ｍｇ系合金、ＪＩＳ　６０００系のＡｌ－Ｍｇ－Ｓｉ系合金等を用いることができる。
　また、本実施形態に係るブレージングシートの心材は、Ｍｎ、Ｓｉ、Ｃｕ、Ｆｅ、Ｔｉ、Ｃｒ、Ｚｒ、Ｌｉをさらに適宜含有していてもよい。 [Heart material]
The core material of the brazing sheet according to the present embodiment is made of an aluminum alloy (including pure aluminum), and more specifically, an aluminum alloy having Mg of 2.0% by mass or less (including 0% by mass). As such an aluminum alloy, an Al-Cu alloy of JIS 2000 series, an Al-Mn alloy of JIS 3000 series, an Al-Mg alloy of JIS 5000 series, an Al-Mg-Si alloy of JIS 6000 series, etc. Can be used.
Moreover, the core material of the brazing sheet according to the present embodiment may further contain Mn, Si, Cu, Fe, Ti, Cr, Zr, and Li as appropriate.
（心材のＭｇ：２．０質量％以下）
　心材のＭｇは、強度を向上させる。また、心材のＭｇは、ろう付加熱時の昇温過程にろう材へ拡散し、ろう溶融温度で雰囲気中に蒸発し、雰囲気中の酸素と反応する。その結果、ろう材表面に形成された酸化膜がＭｇの蒸発時に好適に破壊されるとともに、雰囲気中の酸素濃度が低下し溶融ろうの再酸化が抑制される（ゲッター作用）ことによって、ろう付性を向上させる。なお、ろう材のＭｇもゲッター作用を奏することから、ろう材のＭｇの含有量が多い場合は、心材のＭｇの含有量は少なくてもよく、０質量％であってもよい。
　一方、Ｍｇの含有量が２．０質量％を超えると、ろう材のＢｉによってＭｇをトラップしきれず、ろう材表面でのＭｇＯの生成が促進されてしまい、ろう付性が低下する。
　したがって、心材のＭｇの含有量は、２．０質量％以下（０質量％を含む）である。 (Mg in core: 2.0 mass% or less)
Heartwood Mg improves strength. In addition, Mg of the core material diffuses to the brazing material during the heating process at the time of heat addition to the brazing material, evaporates into the atmosphere at the brazing melting temperature, and reacts with oxygen in the atmosphere. As a result, the oxide film formed on the surface of the brazing material is suitably destroyed at the time of evaporation of Mg, and the oxygen concentration in the atmosphere is lowered to suppress reoxidation of molten brazing (getter action). Improve the quality. In addition, since Mg of the brazing material also exerts a getter action, when the content of Mg of the brazing material is large, the content of Mg of the core material may be small, or may be 0 mass%.
On the other hand, if the content of Mg exceeds 2.0% by mass, the Bi of the brazing material can not trap Mg, the formation of MgO on the surface of the brazing material is promoted, and the brazing property is reduced.
Therefore, the content of Mg in the core material is 2.0% by mass or less (including 0% by mass).
（心材のＭｎ：２．５質量％以下）
　心材のＭｎは、強度を向上させる。ただし、Ｍｎの含有量が２．５質量％を超えると、Ａｌ－Ｍｎ系化合物が多くなり、材料製造工程中に割れが生じるおそれがある。
　したがって、心材にＭｎを含有させる場合、Ｍｎの含有量は、２．５質量％以下である。 (Mn of core material: 2.5 mass% or less)
The core material Mn improves the strength. However, when the content of Mn exceeds 2.5% by mass, the amount of the Al—Mn-based compound increases, and there is a possibility that a crack may occur during the material manufacturing process.
Therefore, when the core material contains Mn, the content of Mn is 2.5% by mass or less.
　なお、Ｍｎを含有させることによって得られる強度の向上という効果をより確実なものとするため、心材のＭｎの含有量は、０．５質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the intensity | strength obtained by containing Mn more reliable, as for content of Mn of a core material, 0.5 mass% or more is preferable.
（心材のＳｉ：１．２質量％以下）
　心材のＳｉは、強度を向上させる。ただし、Ｓｉの含有量が１．２質量％を超えると、心材の固相線温度が低下するため、耐エロージョン性が低下するとともに、ろう流動性が低下するため、ろう付性が低下する。
　したがって、心材にＳｉを含有させる場合、Ｓｉの含有量は１．２質量％以下である。 (Si of core: less than 1.2% by mass)
The core material Si improves the strength. However, if the content of Si exceeds 1.2% by mass, the solidus temperature of the core material is lowered, so that the erosion resistance is lowered and the solderability is lowered, so that the brazing property is lowered.
Accordingly, when the core material contains Si, the content of Si is 1.2% by mass or less.
　なお、Ｓｉを含有させることによって得られる強度の向上という効果をより確実なものとするため、心材のＳｉの含有量は、０．０５質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the strength obtained by containing Si more reliable, as for content of Si of a core material, 0.05 mass% or more is preferable.
（心材のＣｕ：３．０質量％以下）
　心材のＣｕは、心材の電位を貴化させ耐食性を向上させる。ただし、Ｃｕの含有量が３．０質量％を超えると、心材の固相線温度が低下するため、耐エロージョン性が低下するとともに、ろう流動性が低下するため、ろう付性が低下する。
　したがって、心材にＣｕを含有させる場合、Ｃｕの含有量は３．０質量％以下である。 (Cu of core material: 3.0 mass% or less)
The core material Cu makes the potential of the core material noble and improves the corrosion resistance. However, if the content of Cu exceeds 3.0% by mass, the solidus temperature of the core material is lowered, so that the erosion resistance is lowered and the solderability is lowered, so that the brazing property is lowered.
Therefore, when making a core material contain Cu, content of Cu is 3.0 mass% or less.
　なお、Ｃｕを含有させることによって得られる耐食性の向上という効果をより確実なものとするため、心材のＣｕの含有量は、０．０５質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Cu more reliable, as for content of Cu of a core material, 0.05 mass% or more is preferable.
（心材のＦｅ：１．５質量％以下）
　心材のＦｅは、固溶強化作用により強度を向上させる。ただし、Ｆｅの含有量が１．５質量％を超えると、粗大な金属間化合物が形成されることによって、成形性を低下させるおそれがある。
　したがって、心材にＦｅを含有させる場合、Ｆｅの含有量は、１．５質量％以下である。 (Fe in core: less than 1.5% by mass)
The core material Fe improves strength by solid solution strengthening action. However, when the content of Fe exceeds 1.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound.
Therefore, when the core material contains Fe, the content of Fe is 1.5% by mass or less.
　なお、Ｆｅを含有させることによって得られる強度の向上という効果をより確実なものとするため、心材のＦｅの含有量は、０．０５質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the strength obtained by containing Fe more reliable, as for content of Fe of core material, 0.05 mass% or more is preferable.
（心材のＴｉ：０．５質量％以下）
　心材のＴｉは、心材の電位を貴化させ耐食性を向上させる。ただし、Ｔｉの含有量が０．５質量％を超えると、粗大な金属間化合物が形成されることによって、成形性を低下させるおそれがある。
　したがって、心材にＴｉを含有させる場合、Ｔｉの含有量は、０．５質量％以下である。 (Ti: 0.5 mass% or less of core material)
The core material Ti nobles the potential of the core material and improves the corrosion resistance. However, when the content of Ti exceeds 0.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound.
Therefore, when making a core material contain Ti, content of Ti is 0.5 mass% or less.
　なお、Ｔｉを含有させることによって得られる耐食性の向上という効果をより確実なものとするため、心材のＴｉの含有量は、０．０１質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Ti more reliable, as for content of Ti of a core material, 0.01 mass% or more is preferable.
（心材のＣｒ：０．５質量％以下）
　心材のＣｒは、Ａｌ－Ｃｒ系の分散粒子を形成し、心材の強度を向上させる。ただし、Ｃｒの含有量が０．５質量％を超えると、粗大な金属間化合物が形成されることによって、成形性を低下させるおそれがある。
　したがって、心材にＣｒを含有させる場合、Ｃｒの含有量は、０．５質量％以下である。 (Cr of core material: 0.5 mass% or less)
The core material Cr forms dispersed particles of Al-Cr system to improve the strength of the core material. However, when the content of Cr exceeds 0.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound.
Therefore, when making a core material contain Cr, content of Cr is 0.5 mass% or less.
　なお、Ｃｒを含有させることによって得られる強度の向上という効果をより確実なものとするため、心材のＣｒの含有量は、０．０１質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the strength obtained by containing Cr more reliable, as for content of Cr of core material, 0.01 mass% or more is preferable.
（心材のＺｒ：０．５質量％以下）
　心材のＺｒは、Ａｌ－Ｚｒ系の分散粒子を形成し、心材の強度を向上させる。ただし、Ｚｒの含有量が０．５質量％を超えると、粗大な金属間化合物が形成されることによって、成形性を低下させるおそれがある。
　したがって、心材にＺｒを含有させる場合、Ｚｒの含有量は、０．５質量％以下である。 (Zr of core material: 0.5 mass% or less)
The core material Zr forms dispersed particles of Al-Zr system to improve the strength of the core material. However, when the content of Zr exceeds 0.5% by mass, there is a possibility that the formability is reduced due to the formation of a coarse intermetallic compound.
Therefore, when the core material contains Zr, the content of Zr is 0.5% by mass or less.
　なお、Ｚｒを含有させることによって得られる強度の向上という効果をより確実なものとするため、心材のＺｒの含有量は、０．０１質量％以上が好ましい。 In addition, in order to make the effect of the improvement of the strength obtained by containing Zr more reliable, as for content of Zr of a core material, 0.01 mass% or more is preferable.
　前記した心材のＴｉ、Ｃｒ、Ｚｒは、前記した上限値を超えなければ、心材に１種以上、つまり１種が含まれる場合だけでなく、２種以上が含まれていても、本発明の効果を妨げない。 The core material Ti, Cr, and Zr, if not exceeding the upper limit described above, not only when the core material contains one or more types, that is, when one type is included, but two or more types are included in the present invention Do not disturb the effect.
（心材のＬｉ：０．３質量％以下）
　心材のＬｉは、ろう付性をさらに向上させる。Ｌｉがろう付性を向上させる詳細なメカニズムは解明できていないものの、ろう付加熱時のろう溶融時において、Ｌｉがろう材表面に形成された酸化膜を破壊することにより、Ｍｇのゲッター作用をさらに好適に発揮させるのではないかと推測する。ただし、Ｌｉの含有量が０．３質量％を超えると、ろう付け加熱時の昇温過程において、ろう材表層部へＬｉが拡散し酸化膜の成長を促進するためろう付性が低下する。
　したがって、心材にＬｉを含有させる場合、Ｌｉの含有量は、０．３質量％以下である。 (Li of core material: 0.3 mass% or less)
Heartwood Li further improves the brazeability. Although the detailed mechanism by which Li improves the brazeability has not been elucidated, the gettering action of Mg is achieved by the destruction of the oxide film formed on the surface of the brazing material during the brazing heat when the brazing heat is applied. It is speculated that it should be made more effective. However, if the content of Li exceeds 0.3% by mass, Li diffuses into the surface layer of the brazing material in the temperature rising process during brazing heating to promote the growth of the oxide film, and the brazing property decreases.
Therefore, when the core material contains Li, the content of Li is 0.3% by mass or less.
　なお、酸化膜の成長を抑制するという観点から、心材のＬｉの含有量は０．０５質量％以下が好ましい。 From the viewpoint of suppressing the growth of the oxide film, the content of Li in the core material is preferably 0.05% by mass or less.
（心材の残部：Ａｌ及び不可避的不純物）
　心材の残部はＡｌ及び不可避的不純物であるのが好ましい。そして、心材の不可避的不純物としては、Ｖ、Ｎｉ、Ｃａ、Ｎａ、Ｓｒ等が挙げられ、これらの元素は本発明の効果を妨げない範囲で含有されていてもよい。詳細には、Ｖ：０．０５質量％以下、Ｎｉ：０．０５質量％以下、Ｃａ：０．０５質量％以下、Ｎａ：０．０５質量％以下、Ｓｒ：０．０５質量％以下、その他の元素：０．０１質量％未満の範囲で含有されていてもよい。そして、これらについては、前記した所定の含有量を超えなければ、不可避的不純物として含有される場合だけではなく、積極的に添加される場合であっても、本発明の効果を妨げず許容される。
　また、前記したＭｇ、Ｍｎ、Ｓｉ、Ｃｕ、Ｆｅ、Ｔｉ、Ｃｒ、Ｚｒ、Ｌｉについては、積極的に添加してもよいが、不可避的不純物として含まれていてもよい。 (Remaining part of heartwood: Al and unavoidable impurities)
The balance of the core material is preferably Al and unavoidable impurities. And, as the unavoidable impurities of the core material, V, Ni, Ca, Na, Sr, etc. may be mentioned, and these elements may be contained in the range which does not disturb the effect of the present invention. Specifically, V: 0.05% by mass or less, Ni: 0.05% by mass or less, Ca: 0.05% by mass or less, Na: 0.05% by mass or less, Sr: 0.05% by mass or less, and the like The element of: may be contained in a range of less than 0.01% by mass. And about these, if it does not exceed the above-mentioned predetermined content, not only when it is contained as an unavoidable impurity but also when it is added positively, it is acceptable without disturbing the effect of the present invention Ru.
In addition, Mg, Mn, Si, Cu, Fe, Ti, Cr, Zr, and Li may be positively added, but may be contained as unavoidable impurities.
［ろう材］
　本実施形態に係るブレージングシートのろう材は、アルミニウム合金からなり、詳細には、Ｓｉ、Ｂｉ、Ｍｇを含有するアルミニウム合金からなる。このようなアルミニウム合金としては、ＪＩＳ　４０００系のＡｌ－Ｓｉ系合金（Ａｌ－Ｓｉ－Ｍｇ－Ｂｉ系合金）やＡｌ－Ｓｉ－Ｚｎ系合金（Ａｌ－Ｓｉ－Ｚｎ－Ｍｇ－Ｂｉ系合金）等を用いることができる。
　また、本実施形態に係るブレージングシートのろう材は、Ｍｎ、Ｔｉ、Ｃｒ、Ｚｒ、Ｚｎ、Ｓｒ、Ｎａ、Ｓｂ、希土類元素、Ｌｉをさらに適宜含有してもよい。 [Brazed material]
The brazing material of the brazing sheet according to the present embodiment is made of an aluminum alloy, and more specifically, made of an aluminum alloy containing Si, Bi, and Mg. As such aluminum alloys, JIS-4000 Al-Si alloys (Al-Si-Mg-Bi alloys), Al-Si-Zn alloys (Al-Si-Zn-Mg-Bi alloys), etc. Can be used.
In addition, the brazing material of the brazing sheet according to the present embodiment may further contain Mn, Ti, Cr, Zr, Zn, Sr, Na, Sb, a rare earth element, and Li as appropriate.
（ろう材のＳｉ：３質量％以上１３質量％以下、３≦ＣＳｉ≦１３）
　ろう材のＳｉは、ろう材の固相線温度を低下させることによって、ろう付加熱温度での液相率を向上させてろうの流動性を高める。Ｓｉの含有量が３質量％以上であれば、ろうの流動性が高まり、ろう付性の向上という効果が得られる。一方、Ｓｉの含有量が１３質量％を超えると、粗大Ｓｉ粒が形成するとともに、流動ろうが過剰に生成することにより、心材の溶融などのろう付不良が発生するおそれがある。
　したがって、ろう材のＳｉの含有量は、３質量％以上１３質量％以下である。そして、ろう材のＳｉの含有量をＣＳｉ質量％とした場合、３≦ＣＳｉ≦１３である。 (Si: 3 mass% or more and 13 mass% or less of brazing material, 3 ≦ C Si ≦ 13)
By lowering the solidus temperature of the brazing material, the brazing material Si improves the liquid phase rate at the brazing heat addition temperature and enhances the fluidity of the brazing material. When the content of Si is 3% by mass or more, the fluidity of the braze is enhanced, and the effect of improving the brazeability can be obtained. On the other hand, when the content of Si exceeds 13% by mass, coarse Si particles are formed, and excessive flow solder is generated, which may cause brazing failure such as melting of the core material.
Therefore, the content of Si in the brazing material is 3% by mass or more and 13% by mass or less. When the content of Si in the brazing material is C Si mass%, 3 ≦ C Si ≦ 13.
（ろう材のＢｉ：０．１３ＣＭｇ －０．３≦ＣＢｉ≦０．５８ＣＭｇ ０．４５）
　ろう材のＢｉは、心材及びろう材のＭｇと反応し、ろう溶融温度以下ではほとんど溶解しないＭｇ－Ｂｉ系化合物（例えば、Ｂｉ２Ｍｇ３）を生成する。その結果、材料製造工程、及び、ろう付加熱時のろう溶融開始温度までの昇温過程において、Ｍｇのろう材表層部への拡散を抑え、ろう材表面におけるＭｇＯの生成・成長を抑制し（Ｍｇのトラップ作用）、ろう付性を向上させる。また、ろう付加熱時のろう溶融温度では、Ｍｇ－Ｂｉ系化合物は母相（ろう材）に溶解するため、Ｍｇの蒸発が促進される。そして、ろう材表面に形成された酸化膜がＭｇの蒸発時に好適に破壊されるとともに、このＭｇが雰囲気中の酸素と反応することで雰囲気の酸素濃度が低下し溶融ろうの再酸化を抑制する作用（ゲッター作用）が向上し、その結果、ろう付性を向上させる。さらに、Ｂｉは、ろうの流動性を高め、ろう付性を向上させる。 (Brazer Bi: 0.13C Mg- 0.3 ≦ C Bi 0.5 0.58C Mg 0.45 )
The brazing material Bi reacts with the core material and the brazing material Mg to form a Mg—Bi-based compound (eg, Bi 2 Mg 3 ) which hardly dissolves below the brazing material melting temperature. As a result, in the material manufacturing process and the temperature raising process up to the brazing melting start temperature during brazing heat addition, the diffusion of Mg to the brazing filler metal surface layer is suppressed, and the formation and growth of MgO on the brazing filler metal surface are suppressed ( Mg trapping effect), improve the brazeability. In addition, at the solder | pewter melting temperature at the time of heat | fever addition heat | fever, in order that a Mg-Bi type-compound melt | dissolves in a mother phase (brazing | wax material), evaporation of Mg is accelerated | stimulated. Then, the oxide film formed on the surface of the brazing material is suitably destroyed at the time of evaporation of Mg, and this Mg reacts with oxygen in the atmosphere, thereby reducing the oxygen concentration in the atmosphere and suppressing reoxidation of the molten wax. The action (getter action) is improved and as a result, the brazability is improved. Furthermore, Bi improves the fluidity of the braze and improves the brazeability.
　前記した効果を適切に発揮させるためには、ろう材のＢｉの含有量は、心材及びろう材のＭｇの含有量と関係において、非常に精緻に特定する必要がある。
　詳細には、ろう材のＭｇの含有量をＣＭｇ－ｂ質量％、心材のＭｇの含有量をＣＭｇ－ｃ質量％、ＣＭｇ＝ＣＭｇ－ｂ＋ＣＭｇ－ｃ／２とした場合、ろう材のＢｉの含有量が、０．１３ＣＭｇ －０．３未満であると、Ｍｇを十分にトラップできないとともに、ろう材中にフリーなＭｇが多くなる結果、ろう材表面でＭｇＯが生成されてしまう。加えて、ろう材のＢｉの含有量が、０．１３ＣＭｇ －０．３未満であると、ろう流動性が低下し、ろう付性が低下する。
　一方、ろう材のＢｉの含有量が、０．５８ＣＭｇ ０．４５を超えても、ろう付性が低下する。この点について、詳細なメカニズムは解明できていないものの、Ｍｇの含有量に対してＢｉの含有量が多くなると、低融点のＢｉ単体化合物が増え、この化合物がろう付加熱時の低温域から溶融し始め濡れ拡がることで、酸化膜を形成・成長させ、この酸化膜がゲッター作用を抑制してしまうのではないかと推測する。
　したがって、ろう材のＢｉの含有量は、０．１３ＣＭｇ －０．３以上、０．５８ＣＭｇ ０．４５以下である。そして、ろう材のＢｉの含有量をＣＢｉ質量％とした場合、０．１３ＣＭｇ －０．３≦ＣＢｉ≦０．５８ＣＭｇ ０．４５である。 In order to properly exert the above-described effects, the content of Bi in the brazing material needs to be very precisely specified in relation to the content of Mg in the core material and the brazing material.
Specifically, when the content of Mg in the brazing material is CMg-b mass%, the content of Mg in the core material is CMg-c mass%, and CMg = CMg-b + CMg-c / 2, When the content of Bi in the brazing material is less than 0.13 C Mg -0.3 , Mg can not be trapped sufficiently and, as a result, free Mg is increased in the brazing material, so that MgO is generated on the surface of the brazing material. It will In addition, when the content of Bi in the brazing material is less than 0.13 C Mg -0.3 , the brazing flowability decreases and the brazing property decreases.
On the other hand, even if the content of Bi in the brazing material exceeds 0.58 C Mg 0.45 , the brazability decreases. In this respect, although the detailed mechanism has not been elucidated, when the content of Bi increases with respect to the content of Mg, the Bi simple substance having a low melting point increases, and this compound melts from the low temperature range at the time of heat addition. By beginning to wet and spread, an oxide film is formed and grown, and it is speculated that this oxide film may suppress the getter action.
Accordingly, the content of Bi in the brazing material, 0.13C Mg -0.3 or more, 0.58C Mg 0.45 or less. Then, when the content of Bi in the brazing material and C Bi mass%, 0.13C Mg -0.3 ≦ C Bi ≦ 0.58C Mg 0.45.
　「０．１３ＣＭｇ －０．３≦ＣＢｉ≦０．５８ＣＭｇ ０．４５」の係数については、前記のとおり、効果を奏する範囲を特定するためのものであり、多くの実験の結果から導いたものである。 The coefficient of “0.13 C Mg −0.3 ≦ C Bi ≦ 0.58 C Mg 0.45 ” is, as described above, intended to identify the effective range, and is derived from the results of many experiments. It is
（ろう材のＭｇ：０．１質量％以上、ＣＭｇ－ｂ≧０．１）
　ろう材のＭｇは、心材のＭｇと同様、ろう付加熱時のろう溶融温度で雰囲気中に蒸発し、雰囲気中の酸素と反応する。その結果、ろう材表面に形成された酸化膜がＭｇの蒸発時に好適に破壊されるとともに、雰囲気中の酸素濃度が低下し溶融ろうの再酸化が抑制される（ゲッター作用）ことによって、ろう付性を向上させる。なお、心材のＭｇもゲッター作用を奏することから、心材のＭｇの含有量が多い場合は、ろう材のＭｇの含有量は少なくてもよい。
　しかしながら、Ｍｇの含有量が０．１質量％未満であると、熱間圧延時に耳割れが生じやすくなり、ブレージングシートの歩留まりが悪くなってしまう。この点について、詳細なメカニズムは解明できていないものの、ろう材のＭｇの含有量が少ないと、低融点のＢｉ単体化合物が増え、この化合物が熱間圧延時に溶融することで、熱間圧延割れを誘発させるのではないかと推測する。なお、Ｍｇの含有量が０．１質量％以上であると、ＭｇがＢｉと反応し、熱間圧延時にも溶融し難い高融点のＢｉ２Ｍｇ３が生成されることにより、熱間圧延割れの発生を回避することができる。
　したがって、ろう材のＭｇの含有量は、０．１質量％以上である。そして、ろう材のＭｇの含有量をＣＭｇ－ｂ質量％とした場合、ＣＭｇ－ｂ≧０．１である。 (Mg in brazing material: 0.1% by mass or more, C Mg-b 0.1 0.1)
Similar to the core material Mg, the brazing material Mg evaporates into the atmosphere at the brazing material melting temperature at the time of heat addition, and reacts with oxygen in the atmosphere. As a result, the oxide film formed on the surface of the brazing material is suitably destroyed at the time of evaporation of Mg, and the oxygen concentration in the atmosphere is lowered to suppress reoxidation of molten brazing (getter action). Improve the quality. In addition, since Mg of the core material also exerts a getter action, when the content of Mg of the core material is large, the content of Mg of the brazing material may be small.
However, if the content of Mg is less than 0.1% by mass, edge cracking is likely to occur during hot rolling, and the yield of the brazing sheet is degraded. In this respect, although the detailed mechanism has not been elucidated, when the content of Mg in the brazing material is low, the Bi simplex compound with low melting point is increased, and this compound melts during hot rolling, causing hot rolling cracking. Guess that it may cause In addition, when the content of Mg is 0.1 mass% or more, Mg reacts with Bi, and high-melting point Bi 2 Mg 3 which is hardly melted even during hot rolling is generated, thereby causing hot rolling cracking. Can be avoided.
Therefore, the content of Mg in the brazing material is 0.1% by mass or more. And when content of Mg of a brazing filler metal is made into CMg-b mass%, it is CMg-b > = 0.1.
（ろう材のＭｇと心材のＭｇ：０．２≦ＣＭｇ≦１.１）
　ろう材のＭｇと心材のＭｇは、前記したとおり、いずれもゲッター作用を発揮することによって、ろう付性を向上させる。
　ただ、ろう材のＭｇと心材のＭｇとでは、ゲッター作用への寄与度等が異なるため、ゲッター作用に基づくろう付性の向上という効果を適切に発揮させるためには、ろう材のＭｇと心材のＭｇとの含有量を精緻に特定する必要がある。
　ろう材のＭｇの含有量をＣＭｇ－ｂ質量％、心材のＭｇの含有量をＣＭｇ－ｃ質量％、ＣＭｇ＝ＣＭｇ－ｂ＋ＣＭｇ－ｃ／２とした場合、ＣＭｇが０．２未満であると、Ｍｇによるゲッター作用が不十分となり、ろう付性が低下するおそれがある。一方、ＣＭｇが１．１を超えると、ろう材のＢｉによってＭｇをトラップしきれず、ろう材表面でのＭｇＯの生成が促進されてしまい、ろう付性が低下するおそれがある。
　したがって、０．２≦ＣＭｇ≦１.１である。 (Mg of brazing material and Mg of core material: 0.2 ≦ C Mg ≦ 1.1)
As described above, Mg of the brazing material and Mg of the core material both improve the brazeability by exerting a getter function.
However, the contribution to the gettering action differs between Mg of the brazing material and Mg of the core material, so in order to properly exhibit the effect of improving the brazeability based on the gettering action, the Mg of the brazing material and the core material It is necessary to precisely specify the content of Mg and Mg.
When Mg content of the brazing material is CMg -b mass%, that of the core material is CMg-c mass%, and CMg = CMg-b + CMg-c / 2, CMg is 0 If it is less than 2, the gettering effect of Mg may be insufficient, and the brazability may be reduced. On the other hand, if C Mg exceeds 1.1, Bi of the brazing material can not trap Mg, generation of MgO on the surface of the brazing material is promoted, and the brazing property may be reduced.
Therefore, 0.2 ≦ C Mg ≦ 1.1.
　なお、Ｍｇを含有させることによって得られるゲッター作用をより確実なものとするため、ＣＭｇは、０．３以上が好ましい。また、ろう付性の低下を抑制する観点から、ＣＭｇは、０．９以下が好ましい。 In addition, in order to make the getter effect obtained by containing Mg more reliable, C Mg is preferably 0.3 or more. In addition, from the viewpoint of suppressing the decrease in brazing property, C Mg is preferably 0.9 or less.
　「ＣＭｇ＝ＣＭｇ－ｂ＋ＣＭｇ－ｃ／２」の係数については、ろう材のＭｇと心材のＭｇとのゲッター作用への寄与度等を考慮したものであるとともに、前記のとおり、効果を奏する範囲を特定するためのものであり、多くの実験の結果から導いたものである。 The coefficient of “C Mg = C Mg-b + C Mg-c / 2” takes into consideration the degree of contribution to the getter action of Mg of the brazing material and Mg of the core material, and as described above, the effect To identify the range in which the player plays, and is derived from the results of many experiments.
（ろう材のＭｎ：２．０質量％以下）
　ろう材のＭｎは、耐食性を向上させる。Ｍｎが耐食性を向上させる詳細なメカニズムは解明できていないものの、Ａｌ－Ｍｎ－Ｓｉ系化合物が生成され、化合物周囲のＭｎ、Ｓｉ欠乏層が電位の卑な部分となり、優先的に腐食が進行するため、腐食が分散され、耐食性が向上すると推測する。ただし、Ｍｎの含有量が２．０質量％を超えると、Ａｌ－Ｍｎ－Ｓｉ系化合物の生成にＳｉが費やされるため、Ｓｉ濃度が低下し、ろう付性が低下する。
　したがって、ろう材にＭｎを含有させる場合、ろう材のＭｎの含有量は、２．０質量％以下である。 (Mn of brazing material: 2.0% by mass or less)
The brazing material Mn improves the corrosion resistance. Although the detailed mechanism by which Mn improves the corrosion resistance has not been elucidated, Al-Mn-Si compounds are formed, and Mn and Si-depleted layers around the compound become potential dark areas, and corrosion progresses preferentially Therefore, it is presumed that the corrosion is dispersed and the corrosion resistance is improved. However, when the content of Mn exceeds 2.0% by mass, Si is consumed for the formation of an Al-Mn-Si-based compound, so that the Si concentration is lowered and the brazing property is lowered.
Therefore, when the brazing material contains Mn, the content of Mn in the brazing material is 2.0% by mass or less.
　なお、Ｍｎを含有させることによって得られる耐食性の向上という効果をより確実なものとするため、ろう材のＭｎの含有量は、０．０５質量％以上が好ましい。また、Ｓｉ濃度の低下に伴うろう付性の低下を抑制するという観点から、ろう材のＭｎの含有量は、１．２質量％以下が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Mn more reliable, as for content of Mn of a brazing filler material, 0.05 mass% or more is preferable. In addition, from the viewpoint of suppressing a decrease in brazing property due to a decrease in Si concentration, the content of Mn in the brazing material is preferably 1.2% by mass or less.
（ろう材のＴｉ：０．３質量％以下）
　ろう材のＴｉは、耐食性を向上させる。Ｔｉが耐食性を向上させる詳細なメカニズムは解明できていないものの、Ａｌ－Ｔｉ系化合物が生成され、化合物周囲のＴｉ欠乏層が電位の卑な部分となり、優先的に腐食が進行するため、腐食が分散され、耐食性が向上すると推測する。ただし、Ｔｉの含有量が０．３質量％を超えると、溶解、鋳造時に粗大な化合物が生成され、材料製造時に割れが生じやすくなり、製造が困難となる。
　したがって、ろう材にＴｉを含有させる場合、ろう材のＴｉの含有量は、０．３質量％以下である。 (Ti: 0.3 mass% or less of brazing material)
The brazing material Ti improves the corrosion resistance. Although the detailed mechanism by which Ti improves the corrosion resistance has not been elucidated, Al-Ti based compounds are formed, and the Ti-depleted layer around the compound becomes a shallow part of the potential, and the corrosion progresses preferentially, so the corrosion It is estimated that it is dispersed and the corrosion resistance is improved. However, if the content of Ti exceeds 0.3% by mass, coarse compounds are generated during melting and casting, and cracking tends to occur during material production, making production difficult.
Therefore, when the brazing material contains Ti, the content of Ti in the brazing material is 0.3% by mass or less.
　なお、Ｔｉを含有させることによって得られる耐食性の向上という効果をより確実なものとするため、ろう材のＴｉの含有量は、０．０５質量％以上が好ましい。また、材料製造時の割れの発生を抑制するという観点から、ろう材のＴｉの含有量は、０．２質量％以下が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Ti more reliable, as for content of Ti of brazing filler material, 0.05 mass% or more is preferable. In addition, from the viewpoint of suppressing the occurrence of cracking during material production, the content of Ti in the brazing material is preferably 0.2% by mass or less.
（ろう材のＣｒ：０．３質量％以下）
　ろう材のＣｒは、耐食性を向上させる。Ｃｒが耐食性を向上させる詳細なメカニズムは解明できていないものの、Ａｌ－Ｃｒ系やＡｌ－Ｃｒ－Ｓｉ系化合物が生成され、化合物周囲のＣｒ、Ｓｉ欠乏層が電位の卑な部分となり、優先的に腐食が進行するため、腐食が分散され、耐食性が向上すると推測する。ただし、Ｃｒの含有量が０．３質量％を超えると、溶解、鋳造時に粗大な化合物が生成され、材料製造時に割れが生じやすくなり、製造が困難となる。
　したがって、ろう材にＣｒを含有させる場合、ろう材のＣｒの含有量は、０．３質量％以下である。 (Cr of brazing material: 0.3 mass% or less)
The brazing filler metal Cr improves the corrosion resistance. Although the detailed mechanism by which Cr improves the corrosion resistance has not been elucidated, Al-Cr and Al-Cr-Si compounds are formed, and the Cr and Si-depleted layer around the compound becomes a subtle part of the potential, which is preferred. It is assumed that the corrosion progresses and the corrosion is dispersed and the corrosion resistance is improved. However, if the content of Cr exceeds 0.3% by mass, coarse compounds are generated during melting and casting, and cracking tends to occur during material production, making production difficult.
Therefore, when the brazing material contains Cr, the content of Cr in the brazing material is 0.3% by mass or less.
　なお、Ｃｒを含有させることによって得られる耐食性の向上という効果をより確実なものとするため、ろう材のＣｒの含有量は、０．０５質量％以上が好ましい。また、材料製造時の割れの発生を抑制するという観点から、ろう材のＣｒの含有量は、０．２質量％以下が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Cr more reliable, as for content of Cr of brazing filler material, 0.05 mass% or more is preferable. In addition, from the viewpoint of suppressing the occurrence of cracking during material production, the content of Cr in the brazing material is preferably 0.2% by mass or less.
（ろう材のＺｒ：０．３質量％以下）
　ろう材のＺｒは、耐食性を向上させる。Ｚｒが耐食性を向上させる詳細なメカニズムは解明できていないものの、Ａｌ－Ｚｒ系化合物が生成され、化合物周囲のＺｒ欠乏層が電位の卑な部分となり、優先的に腐食が進行するため、腐食が分散され、耐食性が向上すると推測する。ただし、Ｚｒの含有量が０．３質量％を超えると、溶解、鋳造時に粗大な化合物が生成され、材料製造時に割れが生じやすくなり、製造が困難となる。
　したがって、ろう材にＺｒを含有させる場合、ろう材のＺｒの含有量は、０．３質量％以下である。 (Zr of brazing material: 0.3 mass% or less)
The brazing material Zr improves the corrosion resistance. Although the detailed mechanism by which Zr improves the corrosion resistance has not been elucidated, Al-Zr based compounds are formed, and the Zr-depleted layer around the compound becomes a subtle part of the potential, and the corrosion progresses preferentially, so the corrosion is It is estimated that it is dispersed and the corrosion resistance is improved. However, if the content of Zr exceeds 0.3% by mass, coarse compounds are generated during melting and casting, and cracking tends to occur during material production, making production difficult.
Therefore, when the brazing material contains Zr, the content of Zr in the brazing material is 0.3% by mass or less.
　なお、Ｚｒを含有させることによって得られる耐食性の向上という効果をより確実なものとするため、ろう材のＺｒの含有量は、０．０５質量％以上が好ましい。また、材料製造時の割れの発生を抑制するという観点から、ろう材のＺｒの含有量は、０．２質量％以下が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Zr more reliable, as for content of Zr of a brazing material, 0.05 mass% or more is preferable. In addition, from the viewpoint of suppressing the occurrence of cracking during material production, the content of Zr in the brazing material is preferably 0.2% by mass or less.
　前記したろう材のＭｎ、Ｔｉ、Ｃｒ、Ｚｒは、前記した上限値を超えなければ、ろう材に１種以上、つまり１種が含まれる場合だけでなく、２種以上が含まれていても、本発明の効果を妨げない。 If the above-mentioned upper limit values are not exceeded, Mn, Ti, Cr, and Zr of the above-mentioned brazing material are not limited to the case where the brazing material contains one or more kinds, that is, one or two kinds. , Does not interfere with the effects of the present invention.
（ろう材のＺｎ：５．０質量％以下）
　ろう材のＺｎは、ろう材の電位を卑にすることができ、心材との電位差を形成することで犠牲防食効果により耐食性を向上させる。ただし、Ｚｎの含有量が５．０質量％を超えると、フィレットの早期腐食を引き起こすおそれがある。
　したがって、ろう材にＺｎを含有させる場合、ろう材のＺｎの含有量は、５．０質量％以下である。 (Zn of brazing material: 5.0% by mass or less)
Zn of the brazing material can make the potential of the brazing material more strong, and by forming a potential difference with the core material, the corrosion resistance is improved by the sacrificial anticorrosion effect. However, if the content of Zn exceeds 5.0% by mass, premature fillet corrosion may occur.
Therefore, when the brazing material contains Zn, the content of Zn in the brazing material is 5.0% by mass or less.
　なお、Ｚｎを含有させることによって得られる耐食性の向上という効果をより確実なものとするために、ろう材のＺｎの含有量は、０．１質量％以上が好ましい。また、フィレットの早期腐食の発生を抑制するという観点から、ろう材のＺｎの含有量は、４．０質量％以下が好ましい。 In addition, in order to make the effect of the improvement of the corrosion resistance obtained by containing Zn more reliable, as for content of Zn of a brazing material, 0.1 mass% or more is preferable. In addition, from the viewpoint of suppressing the occurrence of premature corrosion of the fillet, the content of Zn of the brazing material is preferably 4.0 mass% or less.
（ろう材のＳｒ：０．１０質量％以下）
　ろう材のＳｒは、共晶Ｓｉを微細化させることにより、ろう付加熱時における心材の溶融の原因となる粗大なＳｉ粒の晶出を抑制する。ただし、Ｓｒの含有量が０．１０質量％を超えると、ろうの流動性が低下し、ろう付加熱時にフィレットの形成が不十分となるおそれがある。
　したがって、ろう材にＳｒを含有させる場合、Ｓｒの含有量は、０．１０質量％以下である。 (Sr of brazing material: 0.10 mass% or less)
The brazing material Sr suppresses crystallization of coarse Si particles which causes melting of the core material at the time of heat addition to a brazing material by refining eutectic Si. However, if the content of Sr exceeds 0.10% by mass, the flowability of the wax may be reduced, and the formation of fillets may be insufficient at the time of heat addition to the wax.
Therefore, when the brazing material contains Sr, the content of Sr is 0.10 mass% or less.
　なお、Ｓｒを含有させることによって得られる共晶Ｓｉの微細化という効果をより確実なものとするため、ろう材のＳｒの含有量は、０．００１質量％以上が好ましい。 In addition, in order to make the effect of refinement | miniaturization of eutectic Si obtained by containing Sr more reliable, content of Sr of a brazing material has preferable 0.001 mass% or more.
（ろう材のＮａ：０．０５０質量％以下）
　ろう材のＮａは、共晶Ｓｉを微細化させることにより、ろう付加熱時における心材の溶融の原因となる粗大なＳｉ粒の晶出を抑制する。ただし、Ｎａの含有量が０．０５０質量％を超えると、ろうの流動性が低下し、ろう付加熱時にフィレットの形成が不十分となるおそれがある。
　したがって、ろう材にＮａを含有させる場合、Ｎａの含有量は、０．０５０質量％以下である。 (Na of brazing material: 0.050 mass% or less)
By refining eutectic Si, the brazing material Na suppresses crystallization of coarse Si particles that causes melting of the core material at the time of heat addition to the brazing material. However, if the content of Na exceeds 0.050% by mass, the flowability of the wax may be reduced, and the formation of fillets may be insufficient at the time of heat addition to the wax.
Therefore, when the brazing material contains Na, the content of Na is 0.050% by mass or less.
　なお、Ｎａを含有させることによって得られる共晶Ｓｉの微細化という効果をより確実なものとするため、ろう材のＮａの含有量は、０．０００１質量％以上が好ましい。 In addition, in order to make the effect of refinement | miniaturization of eutectic Si obtained by containing Na more reliable, as for content of Na of a brazing filler material, 0.0001 mass% or more is preferable.
（ろう材のＳｂ：０．５質量％以下）
　ろう材のＳｂは、共晶Ｓｉを微細化させることにより、ろう付加熱時における心材の溶融の原因となる粗大なＳｉ粒の晶出を抑制する。ただし、Ｓｂの含有量が０．５質量％を超えると、ろうの流動性が低下し、ろう付加熱時にフィレットの形成が不十分となるおそれがある。
　したがって、ろう材にＳｂを含有させる場合、Ｓｂの含有量は、０．５質量％以下である。 (Sb of brazing material: 0.5 mass% or less)
The brazing material Sb suppresses the crystallization of coarse Si particles, which causes melting of the core material at the time of heat addition, by refining eutectic Si. However, if the content of Sb exceeds 0.5% by mass, the fluidity of the wax may be reduced, and the formation of fillets may be insufficient at the time of heat addition to the wax.
Therefore, when the brazing material contains Sb, the content of Sb is 0.5% by mass or less.
　なお、Ｓｂを含有させることによって得られる共晶Ｓｉの微細化という効果をより確実なものとするため、ろう材のＳｂの含有量は、０．００１質量％以上が好ましい。 In addition, in order to make the effect of refinement | miniaturization of eutectic Si obtained by containing Sb more reliable, as for content of Sb of a brazing material, 0.001 mass% or more is preferable.
　前記したろう材のＳｒ、Ｎａ、Ｓｂは、前記した上限値を超えなければ、ろう材に１種以上、つまり１種が含まれる場合だけでなく、２種以上が含まれていても、本発明の効果を妨げない。 If Sr, Na and Sb of the above-mentioned brazing material do not exceed the above-mentioned upper limit value, the brazing material is not limited to one or more kinds, that is, one or two kinds. It does not disturb the effect of the invention.
（ろう材の希土類元素：１．０質量％以下）
　希土類元素とは、周期表３族のうちＳｃとＹにランタノイド（１５元素）を加えた１７元素の総称であり、例えば、Ｓｃ、Ｙ、Ｌａ、Ｃｅ、Ｎｄ、Ｄｙなどが挙げられる。そして、ろう材に希土類元素を含有させる場合、１種が含まれていても、２種以上が含まれていてもよい。なお、ろう材への希土類元素の含有方法は、特に限定されないものの、例えば、Ａｌ－希土類系の中間合金の添加、あるいはミッシュメタルの添加によって２種類以上の希土類元素を同時に含有させることができる。 (Rare earth elements of brazing material: 1.0% by mass or less)
The rare earth element is a generic term of 17 elements of the 3rd group of the periodic table obtained by adding a lanthanoid (15 elements) to Sc and Y, and examples thereof include Sc, Y, La, Ce, Nd and Dy. And when making a brazing material contain a rare earth element, even if it contains 1 type, 2 or more types may be contained. Although the method of containing the rare earth element in the brazing material is not particularly limited, two or more kinds of the rare earth elements can be simultaneously contained by, for example, addition of an Al-rare earth intermediate alloy or addition of misch metal.
　ろう材の希土類元素は、ろう付加熱時に、ろう材の表面酸化膜（Ａｌ２Ｏ３）と希土類元素あるいは希土類元素を含む酸化物が反応し、ろう材の表面酸化膜の体積収縮を生じさせて酸化膜を破壊するため、ろう付性を向上させる。ただし、希土類元素の含有量（２種以上が含まれる場合は総量）が１．０質量％を超えると、希土類元素を含む酸化膜が過剰に生成され、酸化膜破壊の効果が低減するため、ろう付性が低下する。
　したがって、ろう材に希土類元素を含有させる場合、ろう材の希土類元素の含有量は、１．０質量％以下である。 The rare earth element of the brazing material reacts with the surface oxide film (Al 2 O 3 ) of the brazing material and the rare earth element or the oxide containing the rare earth element during heat addition of the brazing material to cause volume contraction of the surface oxide film of the brazing material. Improves the solderability because it destroys the oxide film. However, if the content of the rare earth elements (total amount when two or more are contained) exceeds 1.0% by mass, an oxide film containing the rare earth elements is excessively generated, and the effect of the oxide film destruction is reduced. Brazeability is reduced.
Therefore, when the brazing material contains a rare earth element, the content of the rare earth element in the brazing material is 1.0% by mass or less.
　なお、希土類元素を含有させることによって得られる酸化膜破壊という効果をより確実なものとするため、ろう材の希土類元素の含有量は、０．００１質量％以上が好ましい。 The content of the rare earth element of the brazing material is preferably 0.001% by mass or more in order to further ensure the effect of the oxide film destruction obtained by containing the rare earth element.
（ろう材のＬｉ：０．３質量％以下）
　ろう材のＬｉは、心材のＬｉと同様、ろう付性をさらに向上させる。Ｌｉがろう付性を向上させる詳細なメカニズムは解明できていないものの、ろう付加熱時のろう溶融時において、Ｌｉがろう材表面に形成された酸化膜を破壊することにより、Ｍｇのゲッター作用をさらに好適に発揮させるのではないかと推測する。ただし、Ｌｉの含有量が０．３質量％を超えると、Ｌｉが酸化膜の成長を促進させてしまうためろう付性が低下する。
　したがって、ろう材にＬｉを含有させる場合、Ｌｉの含有量は、０．３質量％以下である。 (Li of brazing material: 0.3 mass% or less)
The brazing material Li, like the core material Li, further improves the brazeability. Although the detailed mechanism by which Li improves the brazeability has not been elucidated, the gettering action of Mg is achieved by the destruction of the oxide film formed on the surface of the brazing material during the brazing heat when the brazing heat is applied. It is speculated that it should be made more effective. However, when the content of Li exceeds 0.3% by mass, Li promotes the growth of the oxide film, and the brazing property is reduced.
Therefore, when the brazing material contains Li, the content of Li is 0.3% by mass or less.
　なお、酸化膜の成長を抑制するという観点から、ろう材のＬｉの含有量は０．０５質量％以下が好ましい。 From the viewpoint of suppressing the growth of the oxide film, the content of Li in the brazing material is preferably 0.05% by mass or less.
（ろう材の残部：Ａｌ及び不可避的不純物）
　ろう材の残部はＡｌ及び不可避的不純物であるのが好ましい。そして、ろう材の不可避的不純物としては、Ｆｅ、Ｃａ、Ｂｅ等が本発明の効果を妨げない範囲で含有されていてもよい。詳細には、Ｆｅ：０．３５質量％以下、Ｃａ：０．０５質量％以下、Ｂｅ：０．０１質量％以下、その他の元素：０．０１質量％未満の範囲で含有されていてもよい。
　そして、これらについては、前記した所定の含有量を超えなければ、不可避的不純物として含有される場合だけではなく、積極的に添加される場合であっても、本発明の効果を妨げず許容される。
　また、前記したＭｎ、Ｔｉ、Ｃｒ、Ｚｒ、Ｚｎ、Ｓｒ、Ｎａ、Ｓｂ、希土類元素、Ｌｉについては、積極的に添加してもよいが、不可避的不純物として含まれていてもよい。 (Remaining part of brazing material: Al and unavoidable impurities)
The balance of the brazing material is preferably Al and unavoidable impurities. And, as an unavoidable impurity of the brazing material, Fe, Ca, Be, etc. may be contained in the range which does not disturb the effect of the present invention. In detail, Fe: 0.35% by mass or less, Ca: 0.05% by mass or less, Be: 0.01% by mass or less, and other elements: less than 0.01% by mass may be contained. .
And about these, if it does not exceed the above-mentioned predetermined content, not only when it is contained as an unavoidable impurity but also when it is added positively, it is acceptable without disturbing the effect of the present invention Ru.
Moreover, about said Mn, Ti, Cr, Zr, Zn, Sr, Na, Sb, rare earth elements, and Li may be added actively, you may contain as an unavoidable impurity.
［アルミニウム合金ブレージングシートの厚さ］
　本実施形態に係るブレージングシートの厚さは、特に限定されないが、チューブ材に用いる場合、０．５ｍｍ以下であるのが好ましく、０．４ｍｍ以下であるのがより好ましく、また、０．０５ｍｍ以上であるのが好ましい。
　そして、本実施形態に係るブレージングシートの厚さは、サイドサポート材、ヘッダー材、タンク材に用いる場合、２．０ｍｍ以下が好ましく、１．５ｍｍ以下がより好ましく、また、０．５ｍｍ以上であるのが好ましい。
　また、本実施形態に係るブレージングシートの厚さは、フィン材に用いる場合、０．２ｍｍ以下であるのが好ましく、０．１５ｍｍ以下であるのがより好ましく、また、０．０１ｍｍ以上であるのが好ましい。
　なお、本実施形態に係るブレージングシートの厚さは、ろう付後強度等の基本特性を損なうことなく適正なろう材の厚さを確保するという観点に基づくと、０．５ｍｍ以上が特に好ましい。 [Thickness of aluminum alloy brazing sheet]
The thickness of the brazing sheet according to the present embodiment is not particularly limited, but when used for a tube material, it is preferably 0.5 mm or less, more preferably 0.4 mm or less, and 0.05 mm or more. Is preferred.
And when using for a side support material, a header material, and a tank material, as for the thickness of the brazing sheet which concerns on this embodiment, 2.0 mm or less is preferable, 1.5 mm or less is more preferable, and 0.5 mm or more Is preferred.
Moreover, when using for a fin material, the thickness of the brazing sheet according to the present embodiment is preferably 0.2 mm or less, more preferably 0.15 mm or less, and 0.01 mm or more. Is preferred.
In addition, the thickness of the brazing sheet according to the present embodiment is particularly preferably 0.5 mm or more based on the viewpoint of securing an appropriate thickness of the brazing material without impairing basic characteristics such as strength after brazing.
　本実施形態に係るブレージングシートのろう材の厚さは、いずれの板材に適用する場合においても特に限定されないが、２μｍ以上が好ましく、５０μｍ以上がより好ましい。
　ろう材の厚さを所定値以上とすることによって、ろう材に含有するＭｇの絶対量が多くなりゲッター作用をより確実に発揮させることができる。なお、ろう材の厚さは、２５０μｍ以下が好ましい。
　本実施形態に係るブレージングシートのろう材のクラッド率は、いずれの板材に適用する場合においても特に限定されないが、４０％以下が好ましく、３０％以下がより好ましい。ろう材のクラッド率を所定値以下とすることによって、ろう付後強度等の基本特性や生産性等の低下を回避・抑制することができる。 Although the thickness of the brazing material of the brazing sheet according to the present embodiment is not particularly limited when applied to any plate material, 2 μm or more is preferable, and 50 μm or more is more preferable.
By setting the thickness of the brazing material to a predetermined value or more, the absolute amount of Mg contained in the brazing material increases, and the getter effect can be more reliably exhibited. The thickness of the brazing material is preferably 250 μm or less.
Although the clad ratio of the brazing material of the brazing sheet according to the present embodiment is not particularly limited when applied to any plate material, 40% or less is preferable, and 30% or less is more preferable. By making the cladding ratio of the brazing material equal to or less than a predetermined value, it is possible to avoid or suppress deterioration of basic characteristics such as strength after brazing and productivity.
［アルミニウム合金ブレージングシートのその他の構成］
　本実施形態に係るブレージングシートについて、図１に示す２層構造の構成を例示して説明したが、その他の構成を除外するものではない。
　例えば、本実施形態に係るブレージングシートの構成は、使用者の要求に応じて、図１に示す心材２の他方側（ろう材３が設けられている側とは逆側）に犠牲材（犠牲防食材、犠材）や中間材を設けてもよい。また、心材２の他方側にろう材をさらに設けてもよい。
　また、心材２の他方側に犠牲材や中間材を設けるとともに、その外側に、ろう材をさらに設けてもよい。
　なお、本実施形態に係るブレージングシートの構成がろう材を心材の両側に備える構成の場合、いずれか一方のろう材が、本発明の発明特定事項を満たせば、他方のろう材は本発明の発明特定事項を満たさないろう材（例えば、ＪＩＳ　４０４５、４０４７、４３４３等のＡｌ－Ｓｉ系合金、Ａｌ－Ｓｉ－Ｚｎ系合金、Ａｌ－Ｓｉ－Ｍｇ系合金等）であってもよい。また、本発明の発明特定事項を満たさないろう材に対しては、当該ろう材表面にフラックスを塗布してろう付してもよい。 [Other configuration of aluminum alloy brazing sheet]
Although the brazing sheet according to the present embodiment has been described by exemplifying the configuration of the two-layer structure shown in FIG. 1, the other configurations are not excluded.
For example, the configuration of the brazing sheet according to the present embodiment is a sacrificial material (sacrificial material) on the other side of the core 2 shown in FIG. 1 (the side opposite to the side on which the brazing material 3 is provided) according to the user's request. An anticorrosive material, a sacrificial material) or an intermediate material may be provided. In addition, a brazing material may be further provided on the other side of the core material 2.
Moreover, while providing a sacrificial material and an intermediate material in the other side of the core material 2, you may further provide brazing material in the outer side.
In the case where the brazing sheet according to the present embodiment is provided with brazing materials on both sides of the core material, if any one of the brazing materials satisfies the invention specific matters of the present invention, the other brazing material of the present invention It may be a brazing material which does not satisfy the invention specific matters (for example, an Al-Si alloy such as JIS 4045, 4047, 4343, an Al-Si-Zn alloy, an Al-Si-Mg alloy, etc.). Moreover, to the brazing material which does not satisfy the invention specific matter of the present invention, flux may be applied to the surface of the brazing material and brazing may be performed.
　犠牲材としては、犠牲防食能を発揮できる公知の成分組成のものであればよく、例えば、ＪＩＳ　１０００系の純アルミニウム、ＪＩＳ　７０００系のＡｌ－Ｚｎ系合金を用いることができる。また、中間材としては、要求特性によって、種々なアルミニウム合金を用いることができる。
　なお、本明細書に示す合金番号は、ＪＩＳ　Ｈ　４０００：２０１４、ＪＩＳ　Ｚ　３２６３：２００２に基づくものである。 Any sacrificial material may be used as long as it has a known component composition capable of exhibiting the sacrificial corrosion preventing ability, and, for example, JIS 1000 pure aluminum and JIS 7000 Al-Zn alloy can be used. Moreover, various aluminum alloys can be used as an intermediate material according to the required characteristics.
In addition, the alloy number shown to this specification is based on JIS H 4000: 2014 and JIS Z 3263: 2002.
　なお、本実施形態に係るブレージングシートは、心材及びろう材の成分と含有量とが特定されていることから、耐食性にも優れる。よって、本実施形態に係るブレージングシートによると、ろう付後の構造体が様々な使用環境・使用雰囲気にも対応することができる。 The brazing sheet according to the present embodiment is excellent in corrosion resistance because the components and contents of the core material and the brazing material are specified. Therefore, according to the brazing sheet according to the present embodiment, the structure after brazing can correspond to various usage environments and atmospheres.
　次に、本実施形態に係るアルミニウム合金ブレージングシートの製造方法について説明する。
［アルミニウム合金ブレージングシートの製造方法］
　本実施形態に係るブレージングシートの製造方法は特に限定されず、例えば公知のクラッド材の製造方法により製造される。以下にその一例を説明する。
　まず、心材、ろう材のそれぞれの成分組成のアルミニウム合金を、溶解、鋳造し、さらに必要に応じて面削（鋳塊の表面平滑化処理）、均質化処理を施して、それぞれの鋳塊を得る。そして、ろう材の鋳塊については、所定厚さまで熱間圧延を施し、心材の鋳塊と組み合わせて、常法にしたがって、熱間圧延によりクラッド材とする。その後、このクラッド材に対して、冷間圧延、必要に応じて中間焼鈍、さらに、最終冷間圧延を施し、必要に応じて最終焼鈍を施す。
　なお、均質化処理は４００～６００℃で１～２０時間、中間焼鈍は３００～４５０℃で１～２０時間実施するのが好ましい。また、最終焼鈍は１５０～４５０℃で１～２０時間実施するのが好ましい。そして、最終焼鈍を実施する場合、中間焼鈍を省略することが可能である。また、調質は、Ｈ１ｎ、Ｈ２ｎ、Ｈ３ｎ、Ｏ（ＪＩＳ　Ｈ　０００１：１９９８）のいずれでもよい。 Next, a method of manufacturing the aluminum alloy brazing sheet according to the present embodiment will be described.
[Method of manufacturing aluminum alloy brazing sheet]
The manufacturing method of the brazing sheet which concerns on this embodiment is not specifically limited, For example, it manufactures by the manufacturing method of a well-known clad material. An example will be described below.
First, melt and cast an aluminum alloy of each composition of core material and brazing material, and if necessary, carry out facing (surface smoothing treatment of ingot) and homogenization treatment, and then give each ingot obtain. Then, the ingot of the brazing material is hot-rolled to a predetermined thickness, combined with the ingot of the core material, and made into a clad material by hot-rolling according to a conventional method. Thereafter, the clad material is subjected to cold rolling, intermediate annealing if necessary, and final cold rolling, and final annealing if necessary.
The homogenization treatment is preferably performed at 400 to 600 ° C. for 1 to 20 hours, and the intermediate annealing is preferably performed at 300 to 450 ° C. for 1 to 20 hours. Also, final annealing is preferably performed at 150 to 450 ° C. for 1 to 20 hours. And when carrying out final annealing, it is possible to omit intermediate annealing. Further, the tempering may be any of H1 n, H2 n, H3 n and O (JIS H 0001: 1998).
　本実施形態に係るアルミニウム合金ブレージングシートの製造方法は、以上説明したとおりであるが、前記各工程において、明示していない条件については、従来公知の条件を用いればよく、前記各工程での処理によって得られる効果を奏する限りにおいて、その条件を適宜変更できることは言うまでもない。 The manufacturing method of the aluminum alloy brazing sheet according to the present embodiment is as described above, but in each of the steps, the conventionally known conditions may be used for the conditions that are not specified, and the treatment in each of the steps is described. It is needless to say that the conditions can be appropriately changed as long as the effects obtained by
　次に、本実施形態に係るアルミニウム合金ブレージングシートのろう付方法について説明する。
［アルミニウム合金ブレージングシートのろう付方法］
　本実施形態に係るアルミニウム合金ブレージングシートのろう付方法は、フラックスを使用しない、いわゆるフラックスレスろう付であって、不活性ガス雰囲気において所定の加熱条件で加熱するという方法である。 Next, the brazing method of the aluminum alloy brazing sheet according to the present embodiment will be described.
[Brazing method of aluminum alloy brazing sheet]
The brazing method of the aluminum alloy brazing sheet according to the present embodiment is so-called fluxless brazing which does not use a flux, and is a method of heating under a predetermined heating condition in an inert gas atmosphere.
（加熱条件：昇温速度）
　本実施形態に係るブレージングシートを加熱（ろう付）する際、３５０℃から５６０℃までの昇温速度が１℃／ｍｉｎ未満であると、この昇温過程において心材及びろう材のＭｇがろう材表層部に過剰に拡散し、ろう材表面においてＭｇＯが生成される可能性が高くなり、ろう付性が低下するおそれがある。一方、３５０℃から５６０℃までの昇温速度が５００℃／ｍｉｎを超えると、この昇温過程において心材及びろう材のＭｇがろう材表層部に適切に拡散せず、ゲッター作用が不十分となる可能性が高くなり、ろう付性が低下するおそれがある。
　したがって、３５０℃から５６０℃までの昇温速度は、１℃／ｍｉｎ以上５００℃／ｍｉｎ以下が好ましい。 (Heating condition: Heating rate)
When heating (brazing) the brazing sheet according to the present embodiment, if the temperature rising rate from 350 ° C. to 560 ° C. is less than 1 ° C./min, Mg in the core material and the brazing material in the temperature rising process is brazing material The excessive diffusion to the surface layer portion increases the possibility that MgO is generated on the surface of the brazing material, which may lower the brazability. On the other hand, when the temperature rising rate from 350 ° C. to 560 ° C. exceeds 500 ° C./min, Mg in the core material and the brazing material does not properly diffuse in the surface layer portion of the brazing material during this temperature rising process, and the getter action is insufficient. And the brazability may be reduced.
Therefore, the temperature rising rate from 350 ° C. to 560 ° C. is preferably 1 ° C./min or more and 500 ° C./min or less.
　なお、ろう材表面におけるＭｇＯが生成される可能性をより低くするため、３５０℃から５６０℃までの昇温速度は、１０℃／ｍｉｎ以上が好ましい。また、ゲッター作用をより確実に発揮させるため、３５０℃から５６０℃までの昇温速度は、３００℃／ｍｉｎ以下が好ましい。
　一方、５６０℃からの降温速度については特に限定されず、例えば、５℃／ｍｉｎ以上１０００℃／ｍｉｎ以下であればよい。 In order to further reduce the possibility of the formation of MgO on the surface of the brazing material, the temperature rising rate from 350 ° C. to 560 ° C. is preferably 10 ° C./min or more. Moreover, in order to exhibit the getter effect more reliably, the temperature rising rate from 350 ° C. to 560 ° C. is preferably 300 ° C./min or less.
On the other hand, the temperature lowering rate from 560 ° C. is not particularly limited, and may be, for example, 5 ° C./min or more and 1000 ° C./min or less.
　５６０℃から実際の加熱温度（後記する加熱温度の範囲内の所定の最高到達温度）までの昇温速度は特に限定されないものの、３５０℃から５６０℃までの昇温速度と同じ範囲内の速度とすればよい。また、実際の加熱温度から５６０℃までの降温速度についても特に限定されないものの、５６０℃からの降温速度と同じ範囲内の速度とすればよい。 Although the heating rate from 560 ° C. to the actual heating temperature (a predetermined maximum temperature within the heating temperature range described later) is not particularly limited, the heating rate within the same range as the heating rate from 350 ° C. to 560 ° C. do it. Further, although the temperature decrease rate from the actual heating temperature to 560 ° C. is not particularly limited, it may be a rate within the same range as the temperature decrease rate from 560 ° C.
（加熱条件：加熱温度、保持時間）
　本実施形態に係るブレージングシートを加熱する際の加熱温度（ろう溶融温度）は、ろう材が適切に溶融する５６０℃以上６２０℃以下であり、５８０℃以上６２０℃以下が好ましい。そして、この温度域における保持時間が１０秒未満であると、ろう付現象（酸化膜の破壊、雰囲気の酸素濃度の低下、接合部への溶融ろうの流動）が生じるのに必要な時間が不足する可能性がある。
　したがって、５６０℃以上６２０℃以下の温度域（好ましくは５８０℃以上６２０℃以下の温度域）における保持時間は、１０秒以上が好ましい。 (Heating conditions: heating temperature, holding time)
The heating temperature (brazing melting temperature) when heating the brazing sheet according to the present embodiment is 560 ° C. or more and 620 ° C. or less at which the brazing material is appropriately melted, and is preferably 580 ° C. or more and 620 ° C. or less. And if the holding time in this temperature range is less than 10 seconds, the time required for the occurrence of brazing phenomenon (destruction of oxide film, reduction of oxygen concentration in the atmosphere, flow of molten solder to the joint) is insufficient there's a possibility that.
Therefore, the holding time in a temperature range of 560 ° C. to 620 ° C. (preferably a temperature range of 580 ° C. to 620 ° C.) is preferably 10 seconds or more.
　なお、ろう付現象をより確実に発生させるため、５６０℃以上６２０℃以下の温度域（好ましくは５８０℃以上６２０℃以下の温度域）における保持時間は、３０秒以上が好ましく、６０秒以上がより好ましい。一方、保持時間の上限については特に限定されないものの、１５００秒以下であればよい。 In order to generate the brazing phenomenon more surely, the holding time in a temperature range of 560 ° C. or more and 620 ° C. (preferably a temperature range of 580 ° C. or more and 620 ° C. or less) is preferably 30 seconds or more and 60 seconds or more. More preferable. On the other hand, although the upper limit of the holding time is not particularly limited, it may be 1500 seconds or less.
（不活性ガス雰囲気）
　本実施形態に係るブレージングシートを加熱（ろう付）する際の雰囲気は、不活性ガス雰囲気であり、例えば、窒素ガス雰囲気、アルゴンガス雰囲気、ヘリウムガス雰囲気、これら複数のガスを混合した混合ガス雰囲気である。また、不活性ガス雰囲気は、酸素濃度が出来る限り低い雰囲気が好ましく、具体的には、酸素濃度は５０ｐｐｍ以下であるのが好ましく、１０ｐｐｍ以下であるのがより好ましい。
　そして、本実施形態に係るアルミニウム合金ブレージングシートのろう付方法は、雰囲気を真空にする必要はなく、常圧（大気圧）で行うことができる。 (Inert gas atmosphere)
The atmosphere at the time of heating (brazing) the brazing sheet according to the present embodiment is an inert gas atmosphere, for example, a nitrogen gas atmosphere, an argon gas atmosphere, a helium gas atmosphere, or a mixed gas atmosphere in which a plurality of these gases are mixed. It is. The inert gas atmosphere is preferably an atmosphere having as low an oxygen concentration as possible. Specifically, the oxygen concentration is preferably 50 ppm or less, more preferably 10 ppm or less.
And the brazing method of the aluminum alloy brazing sheet which concerns on this embodiment does not need to evacuate an atmosphere, and can be performed by a normal pressure (atmospheric pressure).
　なお、通常、本実施形態に係るブレージングシートに対して前記の加熱を施す前（ろう付工程の前）に、被接合部材をブレージングシートのろう材に接するように組み付けることとなる（組み付け工程）。また、組み付け工程の前に、ブレージングシートを所望の形状・構造に成形してもよい（成形工程）。 In addition, usually, before applying the above-mentioned heating to the brazing sheet according to the present embodiment (before the brazing step), the member to be joined is assembled so as to be in contact with the brazing material of the brazing sheet (assembly step) . In addition, the brazing sheet may be formed into a desired shape and structure before the assembling step (forming step).
　本実施形態に係るブレージングシートのろう付方法（言い換えると、ブレージングシートに被接合部材がろう付された構造体の製造方法）は、以上説明したとおりであるが、明示していない条件については、従来公知の条件を用いればよく、前記処理によって得られる効果を奏する限りにおいて、その条件を適宜変更できることは言うまでもない。 The brazing method of the brazing sheet according to the present embodiment (in other words, the method of manufacturing a structure in which the member to be joined is brazed to the brazing sheet) is as described above. Needless to say, conventionally known conditions may be used, and the conditions can be appropriately changed as long as the effects obtained by the treatment can be obtained.
　なお、本実施形態に係るブレージングシートのろう付方法は、使用するブレージングシートの心材及びろう材の成分と含有量とが特定されていることから、優れた耐食性も発揮する。よって、本実施形態に係るブレージングシートのろう付方法によると、ろう付後の構造体が様々な使用環境・使用雰囲気にも対応することができる。 In addition, the brazing method of the brazing sheet according to the present embodiment exhibits excellent corrosion resistance because the components and the contents of the core material and brazing material of the brazing sheet to be used are specified. Therefore, according to the brazing method of the brazing sheet according to the present embodiment, the structure after brazing can correspond to various usage environments and atmospheres.
　次に、本実施形態に係る熱交換器の製造方法について説明する。
［熱交換器の製造方法］
　本実施形態に係る熱交換器の製造方法は、前記したろう付方法を実施するろう付工程を含む方法である。
　なお、本実施形態に係る熱交換器の製造方法は、ろう付工程以外の各工程、例えば、前記した成形工程や組み付け工程等は、従来公知の方法で行えばよい。 Next, a method of manufacturing the heat exchanger according to the present embodiment will be described.
[Method of manufacturing heat exchanger]
The method of manufacturing a heat exchanger according to the present embodiment is a method including a brazing step of performing the above-described brazing method.
In the heat exchanger manufacturing method according to the present embodiment, each process other than the brazing process, for example, the forming process and the assembling process described above may be performed by a conventionally known method.
　次に、本発明に係るアルミニウム合金ブレージングシートのろう付方法について、本発明の要件を満たす実施例と本発明の要件を満たさない比較例とを比較して具体的に説明する。 Next, a method of brazing an aluminum alloy brazing sheet according to the present invention will be specifically described by comparing an example satisfying the requirements of the present invention with a comparative example not satisfying the requirements of the present invention.
［供試材作製］
　表１に示す組成の心材を鋳造し、５００℃×１０時間の均質化処理を施し、所定の厚さまで両面を面削した。また、表２に示す組成のろう材を鋳造し、５００℃×１０時間の均質化処理を施し、所定の厚さまで熱間圧延を施し、熱間圧延板を作製した。そして、心材とろう材とを組み合わせて熱間圧延を施し、クラッド材を得た。その後、冷間圧延を施し、０．４ｍｍの厚さ（ろう材のクラッド率は１０％）とし、４００℃×５時間の最終焼鈍を施し、２層構造のブレージングシート（Ｏ調質材）を作製し、供試材とした。
　なお、供試材Ａ６５、Ａ６６については、前記した厚さと異なる厚さとしたが（供試材Ａ６５の厚さは０．６ｍｍ、ろう材のクラッド率は１０％、供試材Ａ６６の厚さは０．８ｍｍであり、ろう材のクラッド率は１０％）、その他の作製条件は同じであった。 [Sample material preparation]
The core material of the composition shown in Table 1 was casted, subjected to homogenization treatment at 500 ° C. for 10 hours, and chamfered on both sides to a predetermined thickness. Further, a brazing material having a composition shown in Table 2 was cast, homogenized at 500 ° C. for 10 hours, subjected to hot rolling to a predetermined thickness, and a hot-rolled sheet was produced. Then, the core material and the brazing material were combined and subjected to hot rolling to obtain a clad material. Thereafter, cold rolling is performed to obtain a thickness of 0.4 mm (the clad ratio of the brazing material is 10%), final annealing at 400 ° C. for 5 hours is performed, and a two-layered brazing sheet (O-refined material) It manufactured and used as the test material.
In addition, about test material A65 and A66, it was set as the thickness different from the thickness mentioned above (The thickness of test material A65 is 0.6 mm, the clad ratio of brazing material is 10%, the thickness of test material A66 is The clad ratio of the brazing material was 0.8%, and the other preparation conditions were the same.
　次に、ろう付相当加熱の条件、並びに、ろう付性評価、耐食性評価の評価方法及び評価基準を示す。 Next, conditions for brazing-equivalent heating, and evaluation methods and evaluation criteria for evaluation of brazing property and corrosion resistance will be shown.
［ろう付相当加熱］
　ろう付相当加熱は、酸素濃度１０ｐｐｍの窒素雰囲気において、３５０～５６０℃までの昇温速度３０℃／ｍｉｎ、５８０～６２０℃範囲での保持時間１８０ｓ、という条件で実施した。ただし、表４に示す供試材は表中に記載した条件でろう付相当加熱を実施した。
　なお、５６０℃から最高到達温度までの昇温速度は、３５０～５６０℃までの昇温速度と同じであり、降温速度はいずれも１００℃／ｍｉｎであった。 [Brazing equivalent heating]
The brazing equivalent heating was performed in a nitrogen atmosphere with an oxygen concentration of 10 ppm under the conditions of a temperature rising rate of 30 ° C./min from 350 to 560 ° C. and a holding time of 180 s in the 580 to 620 ° C. range. However, the test materials shown in Table 4 carried out brazing equivalent heating under the conditions described in the table.
The temperature rising rate from 560 ° C. to the highest achieved temperature was the same as the temperature rising rate from 350 ° C. to 560 ° C., and the temperature lowering rate was 100 ° C./min.
［ろう付性評価］
　ろう付性は、竹本正ら著、「アルミニウムブレージングハンドブック（改訂版）」（軽金属溶接構造協会、２００３年３月発行）の１３２～１３６頁に記載されている評価方法により評価した。
　詳細には、ろう付相当加熱前の供試材から面寸法が２５ｍｍ×５５ｍｍの試験片を切り出した。そして、図２Ａ、Ｂに示すように、水平に置いた下板１０（３００３Ａｌ合金板（厚さ１．０ｍｍ×縦幅２５ｍｍ×横幅６０ｍｍ））と、この下板１０に対して垂直に立てて配置した上板１１（試験片（縦幅２５ｍｍ×横幅５５ｍｍ））との間に、φ２ｍｍのステンレス製スペーサ１２を挟んで、一定のクリアランスを設定した。また、上板１１をワイヤ１３で固定した。尚、図２Ｂにおける符号１４は「フィレット」である。
　そして、前記したろう付相当加熱の条件でろう付接合した。ろう付接合後、下板と上板の間隙が充填された長さＬ（間隙充填長さ）を測定してろう付性を数値化した。
　なお、このろう付性は、厳密には間隙充填性のことであり、各部材を組み付けたときに生じる部材接合面間の隙間、ろう付時におけるブレージングシートや被接合部材の熱変形の発生により生じる部材接合面間の隙間、を考慮したろう付性である。 [Brazability evaluation]
The brazing property was evaluated by the evaluation method described in Takemoto et al., “Aluminum Brazing Handbook (revised edition)” (March, 2003, published by the Light Metal Welded Structure Association, March 2003).
In detail, the test piece of 25 mm x 55 mm of surface dimensions was cut out from the sample material before brazing equivalent heating. Then, as shown in FIGS. 2A and 2B, the lower plate 10 (3003 Al alloy plate (thickness 1.0 mm × vertical width 25 mm × horizontal width 60 mm)) placed horizontally is erected vertically to the lower plate 10. A fixed clearance was set by sandwiching the stainless steel spacer 12 of φ2 mm between the upper plate 11 (the test piece (vertical width 25 mm × horizontal width 55 mm)) disposed. In addition, the upper plate 11 was fixed by the wire 13. In addition, the code | symbol 14 in FIG. 2B is a "fillet."
And it joined by brazing on the conditions of the above-mentioned brazing equivalent heating. After brazing and bonding, the brazeability was quantified by measuring a length L (gap filling length) in which the gap between the lower and upper plates was filled.
Strictly speaking, this brazing property is the gap filling property, and is caused by the occurrence of thermal deformation of the brazing sheet and the members to be joined at the time of brazing, which are generated when the members are assembled. It is brazability which considered the crevice between member joint surfaces which arises.
　ろう付性評価として、間隙充填長さが４５ｍｍ以上のものを「☆」、３５ｍｍ以上４５ｍｍ未満のものを「◎」、２５ｍｍ以上３５ｍｍ未満のものを「○」、１５ｍｍ以上２５ｍｍ未満のものを「△」、１５ｍｍ未満のものを「×」と評価し、「☆」、「◎」、「○」、「△」を合格、「×」を不合格と評価した。 As the brazing property evaluation, those with a gap filling length of 45 mm or more are “☆”, those with 35 mm or more and less than 45 mm are “◎”, those with 25 mm or more and less than 35 mm are “O”, those with 15 mm or more and less than 25 mm 」", Those less than 15 mm were evaluated as "x", and "☆", "◎", "○", and "Δ" were evaluated as pass and "x" was evaluated as failure.
　表４に示す供試材については、前記したろう付性評価のみ実施したが、表３に示す供試材については、前記したろう付性評価に加えて、以下に示す耐食性評価についても実施した。 For the test materials shown in Table 4, only the brazeability evaluation described above was carried out, but for the test materials shown in Table 3, in addition to the above-described brazing property evaluation, corrosion resistance evaluation shown below was also carried out .
［耐食性評価］
　ろう付相当加熱後の供試材から面寸法が５０ｍｍ×５０ｍｍの試験片を切り出した。この試験片について、ろう材側が試験面（４０ｍｍ×４０ｍｍ）となるように、心材面全体と端面全体およびろう材表面の外縁５ｍｍ幅の領域を、シールテープを用いてシールした。そして、シールした試験片をＯＹ水（Ｃｌ－：１９５質量ｐｐｍ、ＳＯ４ ２－：６０質量ｐｐｍ、Ｃｕ２＋：１質量ｐｐｍ、Ｆｅ３＋：３０質量ｐｐｍ、ｐＨ：３．０）に浸漬し、２０日間、浸漬試験を実施した。詳細には、この浸漬試験は、ＯＹ水を、室温から１時間で８８℃まで加熱し、この８８℃で７時間保持した後、室温まで１時間で冷却し、この室温にて１５時間保持するという一連の流れを１日１サイクルとし、２０日間行うというものであった。
　浸漬試験後、試験面の中でも腐食が最も顕著な領域を光学顕微鏡により断面観察し、腐食形態と腐食深さを求めた。 [Corrosion resistance evaluation]
A test piece with a surface dimension of 50 mm × 50 mm was cut out from the test material after brazing equivalent heating. With respect to this test piece, the entire core surface and the entire end face and a region 5 mm wide at the outer edge of the surface of the brazing material were sealed using a sealing tape so that the brazing material side was a test surface (40 mm × 40 mm). Then, OY The sealed test specimen Water (Cl -: 195 mass ppm, SO 4 2-: 60 mass ppm, Cu 2+: 1 mass ppm, Fe 3+: 30 mass ppm, pH: 3.0) was immersed, The immersion test was carried out for 20 days. Specifically, this immersion test heats OY water from room temperature to 88 ° C. in 1 hour and holds it at this 88 ° C. for 7 hours, then cools to room temperature in 1 hour and holds it at this room temperature for 15 hours A series of flow was made one cycle a day, and it was to be performed for 20 days.
After the immersion test, even in the test surface, the area where corrosion is most prominent was observed with an optical microscope to determine the corrosion form and the corrosion depth.
　耐食性評価として、腐食深さが２５μｍ以下のものを「☆」、２５μｍを超え５０μｍ以下のものを「◎」、５０μｍを超え７５μｍ以下のものを「〇」、７５μｍを超え１００μｍ以下のものを「△」、１００μｍを超えたものを「×」と評価し、「☆」、「◎」、「○」、「△」を合格、「×」を不合格と評価した。
　なお、ろう付性評価が「×」のものについては、耐食性評価を行わなかった。 As corrosion resistance evaluation, those with a corrosion depth of 25 μm or less are “☆”, those exceeding 25 μm to 50 μm or less are “◎”, those exceeding 50 μm to 75 μm are “〇”, those exceeding 75 μm to 100 μm or less 」", And those exceeding 100 μm were evaluated as "x", and "☆", "」 "," ○ ", and" Δ "were evaluated as pass and" x "was evaluated as failure.
In addition, corrosion resistance evaluation was not performed about that whose brazing property evaluation is "x".
　以下、表１には、心材の組成、表２には、ろう材の組成、表３には、供試材の構成、及び、評価結果、表４には、供試材の構成、ろう付条件、及び、評価結果を示す。そして、表１の心材、表２のろう材の残部は、Ａｌ及び不可避的不純物であり、表中の「－」は、含有していない（検出限界以下である）ことを示す。また、表３に示す「０．１３ＣＭｇ ―０．３」、「０．５８ＣＭｇ ０．４５」の値は、小数第３位を四捨五入した値である。 Hereinafter, Table 1 shows the composition of the core material, Table 2 shows the composition of the brazing material, Table 3 shows the composition of the test material, and the evaluation result, Table 4 shows the composition of the test material, brazing The conditions and the evaluation results are shown. And, the core material of Table 1 and the remaining part of the brazing material of Table 2 are Al and unavoidable impurities, and "-" in the table indicates that it does not contain (is below the detection limit). Moreover, the values of “0.13 C Mg −0.3 ” and “0.58 C Mg 0.45 ” shown in Table 3 are values rounded to the third decimal place.
　なお、表３の一部の供試材について、「ＣＢｉ」と「ＣＭｇ」との関係を図３のグラフに示した。また、表３の一部の供試材について、「ＣＭｇ－ｂ」と「ＣＭｇ－ｃ」との関係を図４のグラフに示した。この図３、４中の「○」、「△」については、本発明の規定する要件を満たすものであり、特に「○」は、本発明の規定する好ましい要件を満たすものであり、「×」は本発明の規定する要件を満たさないものである。 Note that some of the test materials shown in Table 3, showing the relationship of "C Bi" and "C Mg" in the graph of FIG. Moreover, the relationship between " CMg-b " and " CMg-c " was shown in the graph of FIG. 4 about a part of test materials of Table 3. FIG. The “o” and “Δ” in FIGS. 3 and 4 satisfy the requirements defined by the present invention, and in particular “o” satisfies the preferred requirements defined by the present invention. "Is not a requirement of the present invention.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000004
Figure JPOXMLDOC01-appb-T000004
［結果の検討］
　供試材Ａ１～Ａ６６、Ｂ１～Ｂ８については、本発明の規定する要件を満たしていた。よって、供試材Ａ１～Ａ６６、Ｂ１～Ｂ８は「ろう付性」が合格という結果となるとともに、供試材Ａ１～Ａ６６は「耐食性」も合格という結果となった。 [Examination of results]
The test materials A1 to A66 and B1 to B8 satisfied the requirements defined by the present invention. Therefore, the test materials A1 to A66 and B1 to B8 resulted in "Brazing property" to pass, and the test materials A1 to A66 resulted in "Corrosion resistance" also to pass.
　そして、本発明の規定する要件を満たすことで「ろう付性」及び「耐食性」が合格であるものは、図３のＣＢｉ＝０．１３ＣＭｇ －０．３、ＣＢｉ＝０．５８ＣＭｇ ０．４５、ＣＭｇ＝０．２、ＣＭｇ＝１．１で囲まれる範囲に位置することがわかった。
　また、本発明の規定する要件を満たすことで「ろう付性」及び「耐食性」が合格であるものは、図４のＣＭｇ－ｃ＝－２ＣＭｇ－ｂ＋０．４とＣＭｇ－ｃ＝－２ＣＭｇ－ｂ＋２．２との間に位置することもわかった。 Then, by satisfying the requirements prescribed in the present invention as "brazing" and "corrosion resistance" is acceptable is, C Bi = 0.13C Mg -0.3 in Fig 3, C Bi = 0.58C Mg It was found to be located in the range enclosed by 0.45 , CMg = 0.2, CMg = 1.1.
In addition, C Mg-c = -2C Mg-b +0.4 and C Mg-c = in FIG. 4 for which "Brazability" and "Corrosion resistance" pass by satisfying the requirements prescribed in the present invention. It was also found to be between -2C Mg-b + 2.2.
　一方、供試材Ａ１００～Ａ１１４については、本発明の規定する要件を満足しないことから、ろう付性が不合格、又は、熱間圧延時に耳割れが発生してしまうという結果となった。詳細には、以下のとおりである。 On the other hand, the test materials A100 to A114 did not satisfy the requirements defined by the present invention, and as a result, the result was that the brazing property failed or that edge cracking occurred during hot rolling. The details are as follows.
　供試材Ａ１００は、ＣＭｇの値が大きく、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０１は、ＣＢｉの値が大きく、Ｂｉ単体化合物に基づく酸化膜がゲッター作用を抑制してしまったと想定され、さらに、ＣＭｇの値が小さく、ゲッター作用が不十分であったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０２は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずに、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０３は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずに、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０４は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずに、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０５は、ＣＢｉの値が大きく、Ｂｉ単体化合物に基づく酸化膜がゲッター作用を抑制してしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０６は、ＣＢｉの値が大きく、Ｂｉ単体化合物に基づく酸化膜がゲッター作用を抑制してしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０７は、ＣＢｉの値が大きく、Ｂｉ単体化合物に基づく酸化膜がゲッター作用を抑制してしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０８は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずにろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１０９は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずに、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、さらに、ＣＭｇの値が小さく、ゲッター作用が不十分であったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１１０は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずに、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１１１は、ＣＭｇの値が大きく、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１１２は、ＣＢｉの値が小さく、Ｍｇを十分にトラップすることができずに、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、さらに、ＣＭｇの値が大きく、ろう材表面でのＭｇＯの生成が促進されてしまったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１１３は、ＣＢｉの値が大きく、Ｂｉ単体化合物に基づく酸化膜がゲッター作用を抑制してしまったと想定され、さらに、ＣＭｇの値が小さく、ゲッター作用が不十分であったと想定され、その結果、ろう付性が「×」となった。
　供試材Ａ１１４は、ＣＭｇ－ｂの値が小さく、Ｂｉ単体化合物が熱間圧延時に溶融し、熱間圧延割れ（耳割れ）を誘発したと想定される。 It is assumed that the test material A100 has a large value of C 2 Mg , and the generation of MgO on the surface of the brazing material is promoted, and as a result, the brazing property becomes “x”.
It is assumed that the test material A101 has a large value of C 2 Bi , and that the oxide film based on the Bi simplex compound has suppressed the gettering action, and further, the value of C 2 Mg is small and the gettering action is insufficient As a result, the brazability became "x".
It is assumed that the test material A102 has a small value of C 2 Bi and can not sufficiently trap Mg, thereby promoting the formation of MgO on the surface of the brazing material. As a result, the brazing property is “ It became "x".
It is assumed that the test material A103 has a small value of C 2 Bi and can not sufficiently trap Mg, thereby promoting the formation of MgO on the surface of the brazing material. As a result, the brazing property is “ It became "x".
It is assumed that the test material A104 has a small value of C 2 Bi and can not trap Mg sufficiently, thereby promoting the formation of MgO on the surface of the brazing material, and as a result, the brazing property is “ It became "x".
It is assumed that the test material A105 has a large value of C 2 Bi , and the oxide film based on the Bi simplex compound has suppressed the getter action, and as a result, the brazing property becomes “x”.
It is assumed that the test material A106 has a large value of C 2 Bi , and the oxide film based on the Bi simplex compound has suppressed the getter action, and as a result, the brazing property becomes “x”.
It is assumed that the test material A107 has a large value of C 2 Bi , and the oxide film based on the Bi simplex compound has suppressed the getter action, and as a result, the brazing property becomes “x”.
It is assumed that sample material A108 has a small value of C 2 Bi and can not sufficiently trap Mg, thereby promoting the formation of MgO on the surface of the brazing material. As a result, the brazing property is “× It became ".
It is assumed that sample material A109 has a small value of C 2 Bi and can not trap Mg sufficiently and that the generation of MgO on the surface of the brazing material is promoted, and further, the value of C 2 Mg is small It was assumed that the gettering action was insufficient, and as a result, the brazeability was "x".
It is assumed that the test material A110 has a small value of C Bi and can not sufficiently trap Mg, and the generation of MgO on the surface of the brazing material is promoted, and as a result, the brazing property is “ It became "x".
The sample material A111 had a large value of C 2 Mg , and was assumed to promote the formation of MgO on the surface of the brazing material, and as a result, the brazing property became “x”.
The sample material A112 is assumed to have a small value of C 2 Bi and to be unable to trap Mg sufficiently and to promote the formation of MgO on the surface of the brazing material. Furthermore, the value of C 2 Mg is large. It was assumed that the formation of MgO on the surface of the brazing material was promoted, and as a result, the brazing property became “x”.
It is assumed that the test material A113 has a large value of C 2 Bi, the oxide film based on the Bi simplex compound has suppressed the gettering action, and further, the value of C 2 Mg is small and the gettering action is insufficient As a result, the brazability became "x".
The sample material A114 has a small value of CMg-b , and it is assumed that the Bi simplex compound melts during hot rolling and induces hot rolling cracking (ear crack).
　以上の結果より、本発明に係るアルミニウム合金ブレージングシートのろう付方法は、
優れたろう付性、及び、耐食性を発揮できることが確認できた。 From the above results, the brazing method of the aluminum alloy brazing sheet according to the present invention,
It has been confirmed that excellent brazability and corrosion resistance can be exhibited.
　本発明を詳細にまた特定の実施態様を参照して説明したが、本発明の精神と範囲を逸脱することなく様々な変更や修正を加えることができることは当業者にとって明らかである。
　本出願は、２０１７年５月２４日出願の日本特許出願（特願２０１７－１０３０７３）に基づくものであり、その内容はここに参照として取り込まれる。 Although the invention has been described in detail and with reference to specific embodiments, it will be apparent to those skilled in the art that various changes and modifications can be made without departing from the spirit and scope of the invention.
This application is based on Japanese Patent Application (Japanese Patent Application No. 2017-103073) filed on May 24, 2017, the contents of which are incorporated herein by reference.
　本発明方法によれば、真空ではない不活性ガス雰囲気でのフラックスレスろう付けのろう付性を向上させることができ、特に熱交換器の製造に有用である。 According to the method of the present invention, it is possible to improve the brazeability of fluxless brazing in an inert gas atmosphere which is not a vacuum, and is particularly useful for the production of a heat exchanger.
１　アルミニウム合金ブレージングシート（ブレージングシート）
２　心材
３　ろう材 1 Aluminum alloy brazing sheet (brazing sheet)
2 heartwood 3 brazing material

Claims (9)

  1. 　心材と、前記心材の少なくとも一方の面に設けられるろう材と、を備えるアルミニウム合金ブレージングシートのろう付方法であって、
    　前記心材は、Ｍｇ：２．０質量％以下（０質量％を含む）であるアルミニウム合金からなり、前記ろう材は、Ｓｉ、Ｂｉ、Ｍｇを含有するアルミニウム合金からなり、
    　前記ろう材のＳｉの含有量をＣＳｉ質量％とし、前記ろう材のＢｉの含有量をＣＢｉ質量％とし、前記ろう材のＭｇの含有量をＣＭｇ－ｂ質量％とし、前記心材のＭｇの含有量をＣＭｇ－ｃ質量％とし、ＣＭｇ＝ＣＭｇ－ｂ＋ＣＭｇ－ｃ／２とした場合に、
    　３≦ＣＳｉ≦１３、
    　０．１３ＣＭｇ －０．３≦ＣＢｉ≦０．５８ＣＭｇ ０．４５、
    　ＣＭｇ－ｂ≧０．１、
    　０．２≦ＣＭｇ≦１.１、を満たし、
    　前記アルミニウム合金ブレージングシートを不活性ガス雰囲気においてフラックスを用いずに５６０～６２０℃の加熱温度によってろう付することを特徴とするアルミニウム合金ブレージングシートのろう付方法。     A brazing method of an aluminum alloy brazing sheet comprising a core material and a brazing material provided on at least one surface of the core material,
    The core material is made of an aluminum alloy that is Mg: 2.0% by mass or less (including 0% by mass), and the brazing material is made of an aluminum alloy containing Si, Bi, and Mg,
    The content of Si of the brazing material and C Si mass%, the content of Bi of the brazing material and C Bi mass%, the content of Mg of the brazing material and C Mg-b wt%, of the core When the content of Mg is C Mg-c mass% and C Mg = C Mg-b + C Mg-c / 2,
    3 ≦ C Si ≦ 13,
    0.13C Mg -0.3 ≦ C Bi ≦ 0.58C Mg 0.45,
    C Mg-b 0.1 0.1,
    Satisfy 0.2 ≦ C Mg ≦ 1.1,
    A method of brazing an aluminum alloy brazing sheet, comprising brazing the aluminum alloy brazing sheet in an inert gas atmosphere at a heating temperature of 560 to 620 ° C. without using a flux.
  2. 　前記ろう材は、更に下記（ａ）～（ｅ）から選ばれる少なくとも一つを含有することを特徴とする請求項１に記載のアルミニウム合金ブレージングシートのろう付方法。
    （ａ）Ｍｎ：２．０質量％以下、Ｔｉ：０．３質量％以下、Ｃｒ：０．３質量％以下、Ｚｒ：０．３質量％以下のうちの１種以上
    （ｂ）Ｚｎ：５．０質量％以下
    （ｃ）Ｓｒ：０．１０質量％以下、Ｎａ：０．０５０質量％以下、Ｓｂ：０．５質量％以下、のうちの１種以上
    （ｄ）希土類元素：１．０質量％以下
    （ｅ）Ｌｉ：０．３質量％以下     The brazing method of an aluminum alloy brazing sheet according to claim 1, wherein the brazing material further contains at least one selected from the following (a) to (e).
    (A) Mn: 2.0% by mass or less, Ti: 0.3% by mass or less, Cr: 0.3% by mass or less, Zr: 0.3% by mass or less (b) Zn: 5 .0 mass% or less (c) Sr: 0.10 mass% or less, Na: 0.050 mass% or less, Sb: 0.5 mass% or less, one or more of (d) rare earth elements: 1.0 Mass% or less (e) Li: 0.3 mass% or less
  3. 　前記心材は、更に下記（ｆ）～（ｋ）から選ばれる少なくとも一つを含有することを特徴とする請求項１に記載のアルミニウム合金ブレージングシートのろう付方法。
    （ｆ）Ｍｎ：２．５質量％以下
    （ｇ）Ｓｉ：１．２質量％以下
    （ｈ）Ｃｕ：３．０質量％以下
    （ｉ）Ｆｅ：１．５質量％以下
    （ｊ）Ｔｉ：０．５質量％以下、Ｃｒ：０．５質量％以下、Ｚｒ：０．５質量％以下の１種以上
    （ｋ）Ｌｉ：０．３質量％以下     The method for brazing an aluminum alloy brazing sheet according to claim 1, wherein the core material further contains at least one selected from the following (f) to (k).
    (F) Mn: 2.5% by mass or less (g) Si: 1.2% by mass or less (h) Cu: 3.0% by mass or less (i) Fe: 1.5% by mass or less (j) Ti: 0 .5% by mass or less, Cr: 0.5% by mass or less, Zr: 0.5% by mass or less (k) Li: 0.3% by mass or less
  4. 　前記心材は、更に下記（ｆ）～（ｋ）から選ばれる少なくとも一つを含有することを特徴とする請求項２に記載のアルミニウム合金ブレージングシートのろう付方法。
    （ｆ）Ｍｎ：２．５質量％以下
    （ｇ）Ｓｉ：１．２質量％以下
    （ｈ）Ｃｕ：３．０質量％以下
    （ｉ）Ｆｅ：１．５質量％以下
    （ｊ）Ｔｉ：０．５質量％以下、Ｃｒ：０．５質量％以下、Ｚｒ：０．５質量％以下の１種以上
    （ｋ）Ｌｉ：０．３質量％以下     The method of brazing an aluminum alloy brazing sheet according to claim 2, wherein the core material further contains at least one selected from the following (f) to (k).
    (F) Mn: 2.5% by mass or less (g) Si: 1.2% by mass or less (h) Cu: 3.0% by mass or less (i) Fe: 1.5% by mass or less (j) Ti: 0 .5% by mass or less, Cr: 0.5% by mass or less, Zr: 0.5% by mass or less (k) Li: 0.3% by mass or less
  5. 　前記ろう材は、厚さが５０μｍ以上であることを特徴とする請求項１に記載のアルミニウム合金ブレージングシートのろう付方法。 The method according to claim 1, wherein the brazing material has a thickness of 50 μm or more.
  6. 　前記ろう材は、厚さが５０μｍ以上であることを特徴とする請求項２に記載のアルミニウム合金ブレージングシートのろう付方法。 The method according to claim 2, wherein the brazing material has a thickness of 50 m or more.
  7. 　前記ろう材は、厚さが５０μｍ以上であることを特徴とする請求項３に記載のアルミニウム合金ブレージングシートのろう付方法。 The method according to claim 3, wherein the brazing material has a thickness of 50 m or more.
  8. 　前記ろう材は、厚さが５０μｍ以上であることを特徴とする請求項４に記載のアルミニウム合金ブレージングシートのろう付方法。 The brazing method of an aluminum alloy brazing sheet according to claim 4, wherein the brazing material has a thickness of 50 μm or more.
  9. 　請求項１から請求項８のいずれか１項に記載のアルミニウム合金ブレージングシートのろう付方法を実施するろう付工程を含むことを特徴とする熱交換器の製造方法。 A method of manufacturing a heat exchanger, comprising a brazing step of performing the brazing method of an aluminum alloy brazing sheet according to any one of claims 1 to 8.
PCT/JP2018/020021 2017-05-24 2018-05-24 Brazing method for aluminum alloy brazing sheet and method for producing heat exchanger WO2018216771A1 (en)

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112176230A (en) * 2019-07-03 2021-01-05 三菱铝株式会社 Aluminum alloy clad material
JP2021159950A (en) * 2020-03-31 2021-10-11 株式会社神戸製鋼所 Aluminum alloy brazing sheet, and, method of brazing aluminum alloy brazing sheet

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111809084A (en) * 2020-07-09 2020-10-23 大力神铝业股份有限公司 High-strength high-ductility composite board material and processing technology thereof

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5619538B2 (en) 1976-12-10 1981-05-08
JP2010247209A (en) * 2009-04-17 2010-11-04 Mitsubishi Alum Co Ltd Fluxless brazing method for aluminum material and aluminum cladding material for fluxless brazing
JP2014050861A (en) * 2012-09-07 2014-03-20 Uacj Corp Aluminum-alloy-made brazing sheet
JP2014155955A (en) * 2013-02-18 2014-08-28 Uacj Corp Brazing sheet for flux-less brazing
JP2014177708A (en) * 2014-05-07 2014-09-25 Uacj Corp Aluminum clad material for heat exchanger
JP5619538B2 (en) * 2010-09-06 2014-11-05 株式会社ティラド Fluxless brazing method of heat exchanger having narrow channel inner fin and aluminum clad material used therefor
JP2016165744A (en) * 2015-03-10 2016-09-15 株式会社Uacj Brazing method for hollow structure
JP2017103073A (en) 2015-12-01 2017-06-08 株式会社オートネットワーク技術研究所 Wire with terminal and manufacturing method of wire with terminal
JP2018099726A (en) * 2016-12-16 2018-06-28 株式会社神戸製鋼所 Brazing method for aluminum alloy brazing sheet

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5602747B2 (en) * 2009-09-21 2014-10-08 株式会社デンソー High corrosion resistance aluminum alloy brazing sheet, method for producing the same, and high corrosion resistance heat exchanger using the same
WO2016017716A1 (en) * 2014-07-30 2016-02-04 株式会社Uacj Aluminium alloy brazing sheet

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5619538B2 (en) 1976-12-10 1981-05-08
JP2010247209A (en) * 2009-04-17 2010-11-04 Mitsubishi Alum Co Ltd Fluxless brazing method for aluminum material and aluminum cladding material for fluxless brazing
JP5619538B2 (en) * 2010-09-06 2014-11-05 株式会社ティラド Fluxless brazing method of heat exchanger having narrow channel inner fin and aluminum clad material used therefor
JP2014050861A (en) * 2012-09-07 2014-03-20 Uacj Corp Aluminum-alloy-made brazing sheet
JP2014155955A (en) * 2013-02-18 2014-08-28 Uacj Corp Brazing sheet for flux-less brazing
JP2014177708A (en) * 2014-05-07 2014-09-25 Uacj Corp Aluminum clad material for heat exchanger
JP2016165744A (en) * 2015-03-10 2016-09-15 株式会社Uacj Brazing method for hollow structure
JP2017103073A (en) 2015-12-01 2017-06-08 株式会社オートネットワーク技術研究所 Wire with terminal and manufacturing method of wire with terminal
JP2018099726A (en) * 2016-12-16 2018-06-28 株式会社神戸製鋼所 Brazing method for aluminum alloy brazing sheet

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
See also references of EP3636380A4
TAKEMOTO TADASHI ET AL.: "Aluminum Brazing Handbook (revised edition", 3 March 2003, JAPAN LIGHT METAL WELDING ASSOCIATION, pages: 132 - 136

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112176230A (en) * 2019-07-03 2021-01-05 三菱铝株式会社 Aluminum alloy clad material
JP2021159950A (en) * 2020-03-31 2021-10-11 株式会社神戸製鋼所 Aluminum alloy brazing sheet, and, method of brazing aluminum alloy brazing sheet
JP7364522B2 (en) 2020-03-31 2023-10-18 株式会社神戸製鋼所 Aluminum alloy brazing sheet and brazing method for aluminum alloy brazing sheet

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